Deposition of boron and carbon containing materials

ABSTRACT

Methods of depositing boron and carbon containing films are provided. In some embodiments, methods of depositing B, C films with desirable properties, such as conformality and etch rate, are provided. One or more boron and/or carbon containing precursors can be decomposed on a substrate at a temperature of less than about 400° C. One or more of the boron and carbon containing films can have a thickness of less than about 30 angstroms. Methods of doping a semiconductor substrate are provided. Doping a semiconductor substrate can include depositing a boron and carbon film over the semiconductor substrate by exposing the substrate to a vapor phase boron precursor at a process temperature of about 300° C. to about 450° C., where the boron precursor includes boron, carbon and hydrogen, and annealing the boron and carbon film at a temperature of about 800° C. to about 1200° C.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation-in-part of U.S. patent application Ser. No. 14/515,341, filed Oct. 15, 2014, entitled “DEPOSITION OF BORON AND CARBON CONTAINING MATERIALS,” which claims the benefit of U.S. Provisional Application No. 61/891,813, filed Oct. 16, 2013, entitled “DEPOSITION OF CONFORMAL SILICON NITRIDE BASED MATERIALS,” the disclosure of each of which is incorporated herein by reference in its entirety.

BACKGROUND

1. Field

The present disclosure relates generally to the field of semiconductor device manufacturing and, more particularly, to deposition of boron and carbon containing materials.

2. Description of the Related Art

Boron and carbon containing materials, such as boron and carbon films, can have a wide variety of uses, including uses in the semiconductor industry. Silicon nitride based materials can be modified to include boron and carbon components, for example forming silicon nitride films comprising boron and carbon components. Boron and carbon films and silicon nitride films comprising boron and carbon components may have various applications in fabrication processes of semiconductor devices.

As the physical geometry of semiconductor devices shrinks, deposition of films on three-dimensional structures having high aspect ratios is desired. Therefore, deposition processes that provide films which can demonstrate conformal coverage of three-dimensional structures having high aspect ratios are desired. Additionally, films are desired that demonstrate an advantageous etch selectivity with respect one or more other materials in the semiconductor device, and/or a desirable etch rate in a dry etch and/or wet etch process.

SUMMARY

In some aspects, methods of forming silicon nitride films comprising boron and carbon are provided. In some embodiments, methods of depositing a silicon nitride based film comprising boron and carbon on a substrate in a reaction space can include contacting the substrate with a vapor-phase silicon reactant to form a layer of the reactant on a surface of the substrate; contacting the surface of the substrate comprising the silicon reactant with a nitrogen reactant; and contacting the substrate with a vapor phase boron and/or carbon reactant. In some embodiments, at least one of contacting the substrate with a vapor-phase silicon reactant, contacting the silicon reactant with a nitrogen precursor, and contacting the substrate with a vapor phase boron reactant are performed two or more times.

Methods of depositing a silicon nitride thin film comprising boron and carbon on a substrate in a reaction space can include exposing the substrate to a vapor-phase silicon precursor; removing excess silicon precursor and reaction byproducts from the reaction space, for example with a purge gas and/or vacuum; contacting the remaining silicon reactant on the substrate surface with a nitrogen precursor; and exposing the substrate to a vapor-phase boron precursor. In some embodiments, at least one of exposing the substrate to a vapor-phase silicon precursor, exposing the substrate to a purge gas and/or a vacuum, contacting the adsorbed silicon reactant with a nitrogen precursor, and exposing the substrate to a vapor-phase boron precursor, can be performed two or more times.

In some aspects, methods of forming boron carbon films are provided. in some embodiments, methods of depositing a boron and carbon film on a substrate in a reaction space can include contacting the substrate with a vapor phase boron precursor at a process temperature of about 325° C. to about 400° C. to form the boron and carbon film on the substrate, where the vapor phase boron precursor decomposes on the substrate.

In some embodiments, methods of forming a boron and carbon film on a substrate in a reaction space can include contacting a three-dimensional structure on the substrate with a vapor phase boron precursor at a process temperature of less than about 400° C. to form the boron and carbon film on the three-dimensional structure, where the boron and carbon film has a step coverage of greater than about 80%. In some embodiments, the methods can include purging the reaction space subsequent to contacting the three-dimensional structure on the substrate with the vapor phase boron precursor.

In some aspects, methods of doping a semiconductor substrate can include depositing a boron and carbon film over the semiconductor substrate in a reaction space by exposing the substrate to a vapor phase boron precursor at a process temperature of about 300° C. to about 450° C., where the boron precursor can include boron, carbon and hydrogen. The boron and carbon film can be annealed at a temperature of about 800° C. to about 1200° C.

In some aspects, methods of doping a substrate can include depositing a boron and carbon film over a substrate in a reaction space using a chemical vapor deposition process. The boron and carbon film can be annealed, for example in a nitrogen atmosphere. In some embodiments no cap layer is formed over the boron and carbon film prior to annealing. In some embodiments, depositing the boron and carbon film can include exposing a substrate comprising a three-dimensional structure to a vapor phase boron precursor in an inert gas atmosphere at a process temperature greater than about 300° C., and purging the reaction space subsequent to exposing the three-dimensional structure on the substrate to the vapor phase boron precursor.

In some aspects, methods of depositing a boron and carbon containing film on a substrate in a reaction space can include contacting the substrate with a vapor phase boron precursor at a process temperature of about 250° C. to about 400° C. to form the boron and carbon containing film on the substrate. In some embodiments the vapor phase boron precursor decomposes on the substrate.

In some embodiments the boron and carbon film has a thickness of less than about 30 angstroms.

For purposes of summarizing the invention and the advantages achieved over the prior art, certain objects and advantages are described herein. Of course, it is to be understood that not necessarily all such objects or advantages need to be achieved in accordance with any particular embodiment. Thus, for example, those skilled in the art will recognize that the invention may be embodied or carried out in a manner that can achieve or optimize one advantage or a group of advantages without necessarily achieving other objects or advantages.

All of these embodiments are intended to be within the scope of the invention herein disclosed. These and other embodiments will become readily apparent to those skilled in the art from the following detailed description having reference to the attached figures, the invention not being limited to any particular disclosed embodiment(s).

BRIEF DESCRIPTION OF THE DRAWINGS

These and other features, aspects, and advantages of the present disclosure are described with reference to the drawings of certain embodiments, which are intended to illustrate certain embodiments and not to limit the invention.

FIG. 1 shows a flow chart of an example of a process for depositing a boron and carbon film, according to an embodiment.

FIGS. 2A and 2B show examples of film stacks comprising boron and carbon films.

FIG. 3 shows a flow chart of another example of a process for depositing a boron and carbon film, according to an embodiment.

FIG. 4 is a graph of the growth rates of boron and carbon films versus process temperatures according to an embodiment.

FIG. 5 is a graph showing fourier transform infrared spectroscopy (FTIR) spectra of a boron and carbon film, deposited according to one embodiment.

FIGS. 6A-6D are SEM images of a boron and carbon film deposited on a high aspect ratio trench structure.

FIG. 7 is a graph showing the removal rate of boron and carbon films when exposed to a wet etchant, according to some embodiments.

FIG. 8 is a graph showing boron and carbon film deposition rates as a function of temperature, according to some embodiments.

FIG. 9A is a STEM image of a cross-sectional view of a boron and carbon film deposited according to an embodiment.

FIG. 9B is a table showing the composition of the boron and carbon film of FIG. 8A.

FIG. 10 is a graph showing Secondary Ion Mass Spectrometry (SIMS) analysis of boron concentration at various depths in a silicon layer in an embodiment in which a boron and carbon film was used as a dopant film as described herein, compared to a BSG film.

FIG. 11 is a graph showing fourier transform infrared spectroscopy (FTIR) spectra of an aging boron and carbon film exposed to a clean room ambient.

FIG. 12 is a table showing optical properties and deposition performances of an example of a boron and carbon film, according to an embodiment.

FIG. 13 shows a flow chart of an example of a process for depositing a silicon nitride film comprising boron and carbon, according to an embodiment.

FIG. 14 shows a flow chart of an example of a process for depositing a silicon nitride film comprising boron and carbon, according to another embodiment.

FIG. 15A is a graph of compositions of examples of silicon nitride films comprising boron and carbon as a function of the percentage of TEB pulses in the deposition process.

FIG. 15B is a graph of film growth rates of examples of silicon nitride films comprising boron and carbon as a function of the percentage of TEB pulses in the deposition process.

FIG. 16 shows FTIR spectra of examples of silicon nitride films comprising boron and carbon.

FIG. 17 shows XRR data of examples of silicon nitride films comprising boron and carbon deposited according to embodiments disclosed herein.

FIG. 18 is a graph of film etch rates of examples of silicon nitride films comprising boron and carbon as a function of the fraction of TEB pulses in the deposition process.

FIGS. 19A-19D are SEM images showing etch performance of an example of a silicon nitride film comprising boron and carbon.

FIGS. 20A-20D are SEM images showing etch performance of an example of a silicon nitride film comprising boron and carbon components.

FIGS. 21A-21D are SEM images showing step coverage of an example of a silicon nitride film comprising boron and carbon components.

DETAILED DESCRIPTION

Although certain embodiments and examples are described below, those of skill in the art will appreciate that the invention extends beyond the specifically disclosed embodiments and/or uses and obvious modifications and equivalents thereof. Thus, it is intended that the scope of the invention herein disclosed should not be limited by any particular embodiments described below.

Films comprising boron and carbon can have a variety of desirable properties, including chemical stability, mechanical strength, and thermal and electrical properties. As a result, such films have diverse applications in many technical fields, including applications in the semiconductor, medical, military, space and nuclear industries. For example, boron carbon films are used as neutron detectors, in the fabrication of semiconductor devices, and in the fabrication of microelectromechanical systems (MEMS). They may be used in tribological coatings for MEMS components and/or as sacrificial films in semiconductor device fabrication processes. In some embodiments, boron and carbon-containing films can be used as a cap layer, an etch stop layer, as a layer for facilitating photolithography patterning processes, and/or as a doping layer (e.g., as a boron dopant source). Other uses outside of the semiconductor area will be apparent to the skilled artisan.

In some embodiments, films comprised essentially of boron and carbon are provided, such as ultrathin boron and carbon films, along with methods of making such materials. For example, in some embodiments, boron and carbon films having a thickness in the sub-nanometers range are provided.

In other embodiments films comprising boron and/or carbon as well as other components are disclosed, along with methods for making such films. For example, in some embodiments silicon nitride films can be formed that include boron and carbon components. Silicon nitride films comprising boron and carbon can have a wide variety of applications, including in semiconductor devices. Silicon nitride films comprising boron and carbon components can form a part of semiconductor devices (e.g., FinFETs), and/or be a part of processes for fabricating semiconductor devices. For example, silicon nitride films comprising boron and carbon components can be deposited on three-dimensional (3-D) features during semiconductor device fabrication processes, for example as a spacer material for a transistor gate feature (e.g., as spacer material of gate features in multi-gate transistors such as FinFETs), and/or as a sacrificial layer in the semiconductor device fabrication process.

As described herein, a boron and carbon (B, C) film can be used in some embodiments as a dopant film in a semiconductor device fabrication process. For example, the boron and carbon film can provide a dopant source for a semiconductor substrate, such as a silicon substrate. In some embodiments, films comprised essentially of boron and carbon can serve as a solid state diffusion (SSD) layer, where the boron can serve as a dopant. For example, the boron and carbon film can be deposited over a substrate and the deposited boron and carbon film can subsequently be subjected to an anneal process such that boron from the boron and carbon film is driven into the underlying substrate.

A cap layer is typically used in conventional solid state doping schemes to reduce or prevent out-diffusion of dopant before, after or during the anneal process. However, in some embodiments, a boron and carbon solid state diffusion layer can advantageously be used as a dopant film without or substantially without a cap layer directly over the boron and carbon solid state diffusion layers. Cap layers used in conventional solid state doping schemes may comprise an oxide and/or a nitride. For example, conventional cap layers may comprise oxides of group 13, 14 or 15 elements, including silicon oxide (e.g., SiO₂) and silicon nitride.

In some embodiments, films comprised essentially of boron and carbon can serve as a cap layer formed over a solid state diffusion layer. For example, a conventionally formed solid state diffusion layer, including a conventionally formed solid state diffusion layer containing boron, can be deposited over a silicon substrate, and a boron and carbon cap layer can be deposited over the conventionally formed solid state diffusion layer, such that the film stack can be subsequently subjected to a thermal anneal process to drive dopant into the underlying silicon substrate. In some embodiments, a boron and carbon cap layer used in conjunction with a conventionally formed solid state diffusion layer can advantageously provide desired dopant concentration within the underlying substrate.

One or more processes described herein may be used to form boron carbon films and/or silicon nitride films comprising boron and carbon, where the films have one or more desirable characteristics, such as a desirable level of conformal coverage of three-dimensional features, a desirable dry etch rate, a desirable wet etch rate, and/or a desirable etch selectivity with respect to another material. In some embodiments, boron carbon films and/or silicon nitride films comprising boron and carbon formed according to one or more processes described herein, can demonstrate desired etch selectivity relative to silicon oxide. As used herein, unless indicated otherwise silicon oxide can have any one of a number of stoichiometric ratios of silicon to oxygen as would be understood by one skilled in the art to be typical for silicon oxides. In some embodiments, silicon oxide can include, but is not limited to, silicon dioxide (SiO₂). Silicon oxide may be formed according to any of various suitable methods, as will be understood by the skilled artisan, and can include for example thermal silicon oxide (TOX) (e.g., a TOX layer in a semiconductor device), chemical silicon oxide and/or native silicon oxide. For example, films deposited according to one or more processes described herein, such as a boron and carbon film or a silicon nitride film comprising boron and carbon, can demonstrate improved step coverage, reduced etch rate in a wet etchant (e.g., resistance against wet etchant, such as a dilute hydrofluoric acid (HF or dHF) solution, such as a 0.5 weight % HF solution), and/or a reduced wet etch ratio with respect to silicon oxide. For example, one or more boron carbon films and/or silicon nitride films comprising boron and carbon described herein may demonstrate a reduced wet etch ratio with respect to a thermal silicon oxide (TOX) (e.g., to provide a ratio of a wet etch rate of the silicon nitride based film to a wet etch rate of the TOX of less than about 1, including less than about 0.5) relative to similar films deposited by other methods.

In some embodiments, a boron and carbon film described herein can be used with another material for enhancing etch selectivity of a resulting structure formed from the boron and carbon film and the other material. For example, in some embodiments, a boron and carbon film described herein can be used as an etch stop layer underneath another layer, or as a cap layer over another layer, where the boron and carbon film is more resistant to certain wet etchants (e.g., dilute HF solution) than the other layer.

In some embodiments, a silicon nitride film including boron and carbon components can have a desirable dielectric constant (κ-value), for example suitable for use as a spacer material for a transistor gate feature. In some embodiments, a silicon nitride film including boron and carbon components can have a dielectric constant of less than about 7, including between about 4.8 and about 7, and between about 4.8 and about 6, as discussed below.

Boron and Carbon Films

As described herein, films comprised primarily of boron and carbon (also referred to boron carbon films, or B, C films, as discussed below) and formed according to one or more processes described herein can advantageously demonstrate various desirable characteristics. In some embodiments, the boron and carbon films can advantageously demonstrate desirable levels of conformality when deposited on three-dimensional (3-D) features of a substrate, such as 3-D features having high aspect ratios. For example, the boron and carbon films may have a conformality of greater than about 90%, including greater than about 95%, when deposited on features having aspect ratios of about 3:1 or higher, including about 10:1 or higher, about 20:1 or higher, about 25:1 or higher, about 40:1 or higher, about 50:1 or higher, or about 80:1 or higher. In some embodiments, the boron and carbon films have a conformality greater than about 90%, including greater than about 95%, when deposited on features having aspect ratios of about 20:1 or greater, including about 40:1 or higher, and about 80:1 or greater.

In some embodiments, the boron and carbon films can demonstrate reduced wet etch rates relative to thermal silicon oxides. For example, the boron and carbon films can demonstrate reduced wet etch rates in dilute hydrofluoric acid solutions (dHF) (e.g., an etch rate of less than about 0.3× that of TOX films exposed to the dHF). In some embodiments, the boron and carbon films can have negligible wet etch rates in dilute HF. In some embodiments, the boron and carbon films have a wet etch rate of less than about 0.2 nanometers per min (nm/min) in dilute HF, preferably less than about 0.1 nm/min, and more preferably less than about 0.05 nm/min. In some embodiments, the boron and carbon films can exhibit etch rates of less than about 0.2 nm/min, preferably less than about 0.1 nm/min, and more preferably less than about 0.05 nm/min, in wet etchants comprising nitric acid (HNO₃) sodium hydroxide (NaOH), hydrochloric acid (HCl) sulfuric acid (H₂SO₄), and/or phosphoric acid (H₃PO₄). In some embodiments the wet etch rate is below the detection limit using one of the recited etchants.

In some embodiments, boron and carbon films formed according to one or more processes described herein demonstrate desirable etch resistance while having a desirable film density, such as film densities of about 2.0 to about 2.5 grams per cubic centimeter (g/cm³). For example, the boron and carbon films may have wet etch rates as described herein while having film densities of about 2.0 g/cm³to about 2.5 g/cm³.

In some embodiments, the boron and carbon films can demonstrate one or more of these desirable characteristics prior to being subjected to a post-deposition treatment process, such as the post-deposition treatment processes that are described in further detail herein. In some embodiments, a post-deposition treatment process further improves one or more of these desirable characteristics.

In some embodiments, a boron and carbon film deposited on a surface comprising silicon (e.g., on a surface of a silicon based layer, such as a silicon layer, a silicon nitride layer, a silicate layer etc.) can demonstrate increased uniformity and/or conformality, such as compared to a boron and carbon film deposited on a surface of a different material (such as a material that does not comprise silicon). For example, a boron and carbon film deposited on a silicon nitride (SiN) surface (e.g., on a surface of a silicon nitride layer, for example on a silicon nitride substrate) can demonstrate increased uniformity. Without being limited by any particular theory or mode of operation, an improved interaction between the silicon-based surface and one or more components of the boron and carbon film may advantageously facilitate the improved uniformity and/or conformality of the deposited film.

As discussed above, a boron and carbon film typically comprises primarily boron and carbon. The formula of a boron and carbon film is generally referred to herein as B, C for convenience and simplicity. However, the skilled artisan will understand that the actual formula of a B, C film can be B_(x)C. In some embodiments, for example, x can vary from about 0.1 to about 25. In some cases, x preferably varies from about 1 to about 10, and more preferably from about 1 to about 2. For example, x can be about 1.5.

In some embodiments, a boron and carbon film is deposited on a substrate by a CVD process comprising decomposing one or more boron precursors (e.g., boron reactants) on a substrate surface at a temperature of less than about 400° C., and at a pressure of about 0.001 Torr to about 760 Torr, including from about 1 Torr to about 10 Torr, or about 0.001 Torr to about 10 Torr. In some embodiments, a boron precursor may comprise both boron and carbon. Thus, in some embodiments a CVD process for depositing a boron and carbon film may include decomposition of a single boron precursor comprising both boron and carbon, without any additional precursors in the deposition process. In some embodiments, a CVD process comprises decomposing two or more precursors on the substrate surface to form the boron and carbon film. In some embodiments, at least one of the two or more precursors comprises boron (B). In some embodiments, at least one of the two or more precursors comprises carbon (C). In some embodiments, the two or more precursors may each comprise boron and carbon. For example, a CVD process for depositing a boron and carbon film may include decomposition of two or more boron precursors, each of the two or more boron precursors comprising both boron and carbon. In some embodiments the CVD process does not include any additional precursors other than the boron precursors (e.g., not including any precursors separately for providing the carbon in the boron and carbon film).

In some embodiments, no or substantially no plasma is used in the deposition of the boron and carbon films (e.g., no or substantially no plasma is used for boron and carbon film growth). In some embodiments, a CVD process may be a pulsed thermal CVD process in which multiple pulses of a single boron precursor are provided to deposit a film of desired thickness. In some embodiments, a single, pulse of the boron precursor is provided to deposit a film of the desired thickness. A thermal CVD process may comprise no plasma or substantially no plasma in the decomposition of precursors. In some embodiments, a purge step may be performed between boron precursor pulses, for example to remove excess reactant and/or reaction byproducts from the reaction space. In some embodiments the substrate may be moved to a space in which it is not exposed to the precursor.

In some embodiments, a boron precursor pulse can comprise one or more carrier gases, such as nitrogen gas and/or a noble gas (e.g., argon gas, helium gas, neon gas, and/or xenon gas). In some embodiments, the boron precursor pulse comprises a mixture of two or more carrier gases. In some embodiments, a mixture of two or more carrier gases comprises argon gas and/or hydrogen gas. For example, a mixture of two or more carrier gases can comprise two or more gases selected from nitrogen gas, helium gas, neon gas, xenon gas, argon gas, and hydrogen gas.

In some embodiments, a process for depositing a boron and carbon film includes a single carrier gas and a single boron precursor, where the single boron precursor comprises both boron and carbon. In some such embodiments the process does not include any other precursors or carrier gases. For example, the single carrier gas may include nitrogen gas (N₂) or a noble gas (e.g., argon (Ar) gas or helium (He) gas). For example, a boron precursor pulse for the process may comprise the single boron precursor and nitrogen gas (N₂), argon (Ar) gas or helium (He) gas. In some embodiments, a process for depositing a boron and carbon film includes a carrier gas mixture and a single boron precursor, where the single boron precursor comprises both boron and carbon. In some such embodiments the process does not include any other gases other than the carrier gas mixture and the single boron precursor. In such embodiments, the carrier mixture may include nitrogen gas (N₂) and a noble gas. For example, the carrier gas mixture may comprise nitrogen gas (N₂) and argon (Ar) or nitrogen gas (N₂) and helium (He). For example, a boron precursor pulse for the process may comprise the single boron precursor and nitrogen gas (N₂) and argon (Ar) gas, or the single boron precursor and nitrogen gas (N₂) and helium (He) gas.

As discussed in further details below, in some embodiments the CVD process is a cyclic deposition process in which reactants are provided cyclically. For example, deposition of a boron and carbon film on a substrate may include two or more deposition cycles in which the substrate is contacted with the reactants to achieve desired film thickness. In other embodiments, the CVD process can be a continuous flow process. For example, deposition of a boron and carbon film on a substrate may include continuously or substantially continuously exposing the substrate to the reactants for a single period of time to achieve desired film thickness.

FIG. 1 shows a flow chart 100 illustrating a process for forming a boron and carbon (B, C) film. In block 102, a substrate is exposed to one or more vapor phase boron reactants (e.g., boron and/or carbon precursors). A carrier gas may be used to transport the one or more vapor phase boron reactants to the substrate. In some embodiments the carrier gas may facilitate one or more interactions between reactants and/or between reactants and the substrate surface for forming the boron and carbon film, while not or substantially not contributing to growth of the boron and carbon film.

In some embodiments, the substrate is exposed to a single vapor phase boron reactant. In some embodiments, the single vapor phase boron reactant comprises both boron (B) and carbon (C). In some embodiments, the substrate is exposed to two or more vapor phase reactants. For example, at least one of the two or more vapor phase reactants comprises carbon (C) and at least one of the two or more vapor phase reactants comprises boron (B).

In some embodiments, the carrier gas can comprise an inert carrier gas, such as argon (Ar), nitrogen gas (N₂), helium (He), xenon (Xe) and/or neon (Ne). In some embodiments, the carrier gas can comprise a mixture of two or more gases, including two or more gases selected from nitrogen gas, helium gas, neon gas, xenon gas, argon gas, and hydrogen gas. In block 104, exposure of the substrate to the carrier gas and the one or more vapor phase boron reactants can be repeated a number of times, such as in a pulsed CVD process. For example, the substrate can be exposed to the carrier gas and the one or more vapor phase boron reactants for a first duration of time, and the exposure may be repeated about 5 times to about 5,000 times, including about 100 times to about 3,000 times, including about 1000 times, and about 2,000 times. In some embodiments, the exposure can be repeated less than about 100 times, including from about 1 to about 100 times, about 2 to about 50 times, about 3 to about 20 times, or about 5 to about 10 times.

The duration of time may be the same in each of the repetitions, or cycles, or may vary between one or more cycles. The number of repetitions can be selected to facilitate deposition of a boron and carbon film of a desired thickness, for example. In some embodiments, an exposure of the substrate to the carrier gas and the one or more vapor phase boron reactants may be followed by discontinuing flow of the one or more vapor phase boron reactants into the reaction space. In some embodiments, an exposure of the substrate to the carrier gas and the one or more vapor phase boron reactants can be followed by a purge step and/or transport of the substrate to a space away from the reactants (e.g., such that the substrate is not or substantially not exposed to the reactants). The purge step may be configured to remove one or more excess reactants and/or reaction byproducts from the reactor chamber. In some embodiments, a purge step and/or transport of the substrate follows each exposure of the substrate to the carrier gas and the one or more vapor phase boron reactants. For example, subsequent to each exposure of the substrate to the reactant(s) in each cycle, the substrate may be moved to a space free or substantially free of the reactants, or the reactor may be purged of excess reactants and/or reaction byproducts. In some embodiments, the purge step comprises continuing flow of the carrier gas (e.g., continuing flow of the carrier gas, such as at least one component of a multi-component carrier gas, at a same or different flow rate as compared to that during the reactant pulse). For example, a process 100 for depositing boron and carbon films may include continuously flowing the carrier gas while periodically flowing the one or more vapor phase boron reactants.

In some embodiments a process for depositing a boron and carbon (B, C) film may include a chemical vapor deposition (CVD) process. Referring to FIG. 1, in some embodiments the process 100 includes a thermal CVD process performed at reduced process temperatures, for example temperatures less than about 400° C. A thermal CVD process can be a process in which no or substantially no plasma is applied, such as for facilitating decomposition of precursors used to deposit the film. The process temperature as referred to herein can comprise a temperature of a reactor chamber susceptor, a reactor chamber wall, and/or a temperature of the substrate itself. For example, in some embodiments the process 100 for depositing the boron and carbon film can be performed with a process temperature of up to about 400° C. In some embodiments, the process 100 for depositing the boron and carbon film can be performed with a process temperature of about 325° C. to about 400° C., preferably about 350° C. to about 400° C., and most preferably about 375° C. to about 400° C. Without being limited by any particular theory or mode of operation, deposition of boron and carbon films at temperatures less than about 400° C. may advantageously facilitate deposition in a surface reaction limited regime, facilitating formation of boron and carbon films having one or more desirable characteristics described herein (e.g., increased conformality performance, increased uniformity, and/or decreased etch rate).

In some embodiments, deposition of boron and carbon films (B, C) can be performed at process temperatures of about 200° C. to about 450° C., including for example, about 250° C. to about 400° C., or about 400° C. to about 425° C.

In some embodiments, deposition of boron and carbon films (B, C) can be performed, such as in single wafer reactors, at process temperatures of up to about 450° C., including about 300° C. to about 450° C., or about 400° C. to about 425° C. For example, in some embodiments a boron and carbon film can be deposited at process temperatures of about 400° C. to about 450° C., such as at about 430° C. For example, deposition of boron and carbon films in single wafer reactors can be performed at process temperatures of about 400° C. to about 425° C.

In some embodiments, deposition of boron and carbon films (B, C) can be performed at process temperatures of up to about 400° C. For example, in some embodiments, deposition of boron and carbon films (B, C) in batch reactors can be performed at process temperatures of about 250° C. to about 400° C., preferably about 275° C. to about 375° C., and more preferably about 300° C. to about 350° C.

According to some embodiments of the present disclosure, the pressure of the reactor chamber during processing is maintained at about 0.001 Torr to about 760 Torr, including about 0.01 Torr to about 50 Torr, preferably from about 0.1 Torr to about 10 Torr, and more preferably from about 1 Torr to about 10 Torr. In some embodiments, deposition of boron and carbon films can be performed with a reactor chamber pressure of about 0.5 Torr to about 8 Torr. For example, the reactor chamber pressure may be about 6 Torr. The selected reaction chamber pressure may serve to facilitate formation of the desired boron and carbon films. In some embodiments, the chamber pressure may be selected based on a configuration of the reactor chamber (e.g., a batch reactor or a single wafer reactor). In some embodiments, a batch reactor may have a reactor chamber pressure from about 0.001 Torr to about 10 Torr. In some embodiments, the chamber pressure may be selected to provide a boron and carbon film which has desired conformality and/or etch rate performances.

As described herein, a carrier gas may comprise an inert carrier gas, such as nitrogen gas (N₂), helium (He), xenon (Xe) and/or neon (Ne). For example, block 102 of FIG. 1 may include exposing a substrate to one or more boron reactants and nitrogen gas. Without being limited by any particular theory or mode of operation, nitrogen gas, helium, xenon, and neon can exhibit an increased thermal conductivity (e.g., for example a greater thermal conductivity as compared to that of other inert carrier gases, such as argon (Ar)), thereby facilitating decomposition of the one or more boron and/or carbon precursors. Further, without being limited by any particular theory or mode of operation, a carrier gas having an increased thermal conductivity may facilitate decomposition of the one or more boron and/or carbon precursors in high aspect ratio features of a 3-D substrate surface, facilitating formation of a conformal and/or etch resistant boron and carbon film over the high aspect ratio features. For example, use of carrier gas comprising nitrogen gas, helium, xenon, and/or neon, including carrier gas mixtures comprising two or more of nitrogen gas, helium, xenon, neon, argon and/or hydrogen, may facilitate formation of a conformal and/or etch resistant boron and carbon film.

In some embodiments, a carrier gas may comprise argon (Ar). For example, block 102 of FIG. 1 may include exposing a substrate to one or more vapor phase boron reactants and argon gas.

In some embodiments, flow of one or more of the vapor phase boron reactants into the reaction space can be continuous or substantially continuous. For example, a process 100 for depositing the boron and carbon (B, C) film may comprise a continuous flow thermal CVD process. For example, flow of the one or more vapor phase boron reactants into the reaction chamber can be continued until a desired boron and carbon film thickness is achieved. In some embodiments, the flow rate of a boron reactant and/or carrier gas may be varied during a continuous flow thermal CVD process to provide the desired boron and carbon film. In some embodiments, a process temperature and/or reactor chamber pressure may be varied during a continuous flow thermal CVD process to provide the desired boron and carbon film.

In some embodiments, process 100 for depositing the boron and carbon (B, C) film comprises a pulsed thermal CVD process. In some embodiments, the process 100 may comprise a cyclic deposition process. For example, a cycle of the process 100 may comprise contacting the substrate with a reactant for a desired amount of time, such as by supplying into the reactor chamber a reactant pulse for a desired duration. The reactant pulse may comprise a carrier gas (e.g., argon, nitrogen gas, helium and/or neon) and at least one or more boron reactants. In some embodiments, the reactant pulse is repeated a number of times to deposit a boron and carbon film of desired thickness and/or composition (e.g., repetition of a number of cycles, each cycle comprising the reactant pulse).

In some embodiments one or more reactant pulses can be followed by a step in which the substrate is not exposed to the reactant(s), such as a purge step and/or transport of the substrate into a space free or substantially free of the reactants. For example, the substrate may first be transported to a space free or substantially free of the reactants and the reactor chamber may then be purged of any excess reactants and/or reaction byproducts. In some embodiments each reactant pulse of a plurality of reactant pulses may be followed by a purge step and/or transport of the substrate to a space free or substantially free of the reactants. The purge step may be configured to remove one or more excess reactants and/or reaction byproducts from the reactor chamber. For example, a purge step may comprise flowing one or more purge gases through the reactor chamber, and/or evacuating the reactor chamber to remove or substantially remove excess reactants and/or reaction byproducts (e.g., by drawing a vacuum upon the reactor chamber). In some embodiments, the purge gas comprises an inert gas. In some embodiments, the purge gas comprises nitrogen gas. In some embodiments, the purge gas comprises a noble gas. In some embodiments, the purge gas comprises argon gas.

In some embodiments, a reactant pulse can be followed by discontinuing flow of the one or more vapor phase boron reactants into the reactor chamber while continuing flow of the carrier gas. For example, a purge step may comprise continued flow of the carrier gas (e.g., at a same or different flow rate, such as a higher flow rate, as compared to that during the reactant pulse) in order to remove reactant from the reaction chamber. In some embodiments, a purge step may comprise continuing flow of at least one component of a carrier gas comprising a mixture of two or more gases for removing excess reactant from the reactor chamber. In some embodiments, a process 100 for depositing boron and carbon films may include continuously flowing the carrier gas while alternating flow of the one or more vapor phase boron reactants.

A duration of the reactant pulse can be selected to provide a desired quantity of the one or more boron reactants into the reactor chamber and/or a desired amount of deposition. In some embodiments, a reactant pulse can have a duration of about 0.1 seconds (s) to about 5 s, including about 0.1 s to about 1 s. For example, a reactant pulse can have a duration of about 0.5 s. In some embodiments, a reactant pulse can have a duration of about 0.3 s.

In some embodiments, an interval between reactant pulses can be about 1 s to about 15 s. In some embodiments, the interval comprises a purge step for removing excess reactants and/or reaction byproducts from the reactor chamber. In some embodiments, the interval comprises transport of the substrate to a space free or substantially free of reactants. For example, the interval may comprise transport of the substrate to a space free or substantially free of reactants, and a purge step having a duration of about 0.5 s to about 15 s, including about 1 s to about 10 s. For example, the purge step can have a duration of about 5 s. In some embodiments, the purge step can have a duration of about 1 s.

In some embodiments, a duration of the reactant pulse and/or the interval between reactant pulses (e.g., including for example, duration of a purge step) can be selected based a surface area of the substrate on which the boron and carbon film is deposited, an aspect ratio of a three dimensional (3-D) structure on which the boron and carbon film is deposited, and/or a configuration of the reactor chamber. For example, the reactant pulse and/or the interval between reactant pulses may have an increased duration for depositing a boron and carbon film on a larger surface area, 3-D structures having increased aspect ratios, and/or for deposition in a batch reactor. In some embodiments, an increased reactant pulse duration and/or interval between reactant pulses is selected for deposition on ultra-high aspect ratio features, including for example, features having aspect ratios of about 40:1 and greater, including about 80:1 and greater.

In some embodiments, the one or more boron reactants are supplied into the reactor chamber from a respective source container in which the reactants are stored in vapor form. Vapor pressure of each reactant can facilitate delivery of the reactant into the reactor chamber. For example, the vaporized reactants can be provided into the reactor chamber using a vapor draw technique. In some embodiments, a source container can be maintained at a temperature of about 20° C. to about 25° C. A mass flow rate of a vaporized reactant into the reactor chamber may be controlled, for example, by controlling the extent to which a supply valve for providing the vaporized reactant into the reactor chamber is kept open.

In some embodiments, a suitable boron reactant may include one or more compounds comprising a B—C bond. In some embodiments, a suitable boron reactant can include a boron compound having at least one organic ligand. In some embodiments, the organic ligand can have double and/or triple bonds. In some embodiments, the organic ligand can be a cyclic ligand. In some embodiments, the organic ligand can comprise delocalized electrons. In some embodiments, a suitable boron reactant can include trialkylboron compounds. In some embodiments, a suitable boron reactant can include triethylboron (B(C₂H₅)₃, TEB). In some embodiments, a suitable boron reactant can include trimethylboron (B(CH₃)₃, TMB). In some embodiments, a suitable boron reactant can include trialkylboron compounds having linear or branched alkyl groups, including for example linear or branched C3-C8, and more preferably including linear or branched C3-C5. Suitable boron reactants can include a variety of other boron-containing reactants. In some embodiments, a boron reactant can include a boron halide, an alkylboron, and/or a borane. In some embodiments, a boron reactant can include boron halides, borane halides and complexes thereof. For example, a suitable boron halide can have a boron to halide ratio of about 0.5 to about 1.

Suitable boranes can include compounds according to formula I or formula II.

B_(n)H_(n+x)   (formula I)

Wherein n is an integer from 1 to 10, preferably from 2 to 6, and x is an even integer, preferably 4, 6 or 8.

B_(n)H_(m)   (formula II)

Wherein n is an integer from 1 to 10, preferably form 2 to 6, and m is an integer different than n, from 1 to 10, preferably from 2 to 6.

Of the above boranes according to formula I, examples include nido-boranes (B_(n)H_(n+4)), arachno-boranes (B_(n)H_(n+6)) and hyph-boranes (B_(n)H_(n+8)). Of the boranes according to formula II, examples include conjuncto-boranes (B_(n)H_(m)). Also, borane complexes such as (CH₃CH₂)₃N—BH₃ can be used.

In some embodiments, suitable boron reactants can include borane halides, particularly fluorides, bromides and chlorides. An example of a suitable compound is B₂H₅Br. Further examples comprise boron halides with a high boron/halide ratio, such as B₂F₄, B₂C₁₄ and B₂Br₄. It is also possible to use borane halide complexes.

In some embodiments, halogenoboranes according to formula III can be suitable boron reactants.

B_(n)X_(n)   (formula III)

Wherein X is Cl or Br and n is 4 or an integer from 8 to 12 when X is Cl, or n is an integer from 7 to 10 when X is Br.

In some embodiments, carboranes according to formula IV can be suitable boron reactants.

C₂B_(n)H_(n+x)   (formula IV)

Examples of carboranes according to formula IV include closo-carboranes (C₂B_(n)H_(n+2)), nido-carboranes (C₂B_(n)H_(n+4)) and arachno-carboranes (C₂B_(n)H_(n+6)).

In some embodiments, amine-borane adducts according to formula V can be suitable boron reactants.

R₃NBX₃   (formula V)

Wherein R is linear or branched C1 to C10, preferably C1 to C4 alkyl or H, and X is linear or branched C1 to C10, preferably C1 to C4 alkyl, H or halogen.

In some embodiments, aminoboranes where one or more of the substituents on B is an amino group according to formula VI can be suitable boron reactants.

R₂N   (formula VI)

Wherein R is linear or branched C1 to C10, preferably C1 to C4 alkyl or substituted or unsubstituted aryl group.

An example of a suitable aminoborane is (CH₃)₂NB(CH₃)₂.

In some embodiments, a suitable boron reactant can include a cyclic borazine (—BH—NH—)₃ and/or its volatile derivatives.

In some embodiments, alkyl borons or alkyl boranes can be suitable boron reactants, wherein the alkyl is typically linear or branched C1 to C10 alkyl, preferably C2 to C4 alkyl.

According to some embodiments, a process for depositing a boron and carbon (B, C) film comprises a pulsed thermal CVD process performed at a process temperature of about 375° C. to about 400° C., and at a pressure of about 0.5 Torr to about 3 Torr. The process may include contacting the substrate with a reactant pulse comprising nitrogen gas as the carrier gas and triethylboron (TEB) as the boron and carbon reactant. The supply of TEB may be drawn from a source container for storing TEB at a temperature of about 20° C. to about 25° C. (e.g., a needle valve for providing TEB flow into the reactor chamber may be kept open at about two turns). The reactant pulse may have a duration of about 0.5 s. In some embodiments a single cycle of the process may include the reactant pulse followed by a period of time in which the substrate is not exposed to the reactant, such as a purge step. The purge step may comprise flowing nitrogen gas without the reactant, for example for a duration of about 5 s. The process may include repeating the cycle comprising the reactant pulse followed by the purge step a number of times to achieve a boron and carbon film of a desired thickness and/or composition. For example, the cycle may be repeated up to about 1,000 times, about 1,500 times, about 2,000 times, or about 5,000. In some embodiments, the cycle can be repeated about 2 to about 1,000 times, including about 2 to about 2,000 times, about 3 to about 2,000 times, or about 5 to about 5,000 times. In some embodiments, the cycle can be repeated about 50 to about 2,000 times. In some embodiments, the cycle can be repeated about 100 to about 1,500 times. In some embodiments, the cycle can be repeated up to about 100 times. In some embodiments, the cycle can be repeated from about 1 to about 100 times, about 10 to about 100 times. In some embodiments, the cycle can be repeated about 2 to about 50 times, about 3 to about 20 times, or about 5 to about 10 times.

One or more boron and carbon (B, C) films formed according to one or more processes described herein may advantageously demonstrate desired conformality, such as when deposited on high aspect ratio features of 3-D substrate surfaces, and/or desired etch rate performances (e.g., wet etch rate performance, such as wet etch rate performance in dilute HF solution). The films may also exhibit a reduced film density, such as film densities of about 2.0 grams per cubic centimeter (g/cm³) to about 2.5 g/cm³. In some embodiments, the boron and carbon films can demonstrate a conformality of greater than about 80%, preferably greater than about 90% and more preferably greater than about 95%, for example when the boron and carbon films are formed on 3-D structures having aspect ratios of about 3:1 or higher, including about 10:1 or higher, about 25:1 or higher, or about 50:1 or higher. In some embodiments, the boron and carbon films can demonstrate a conformality of greater than about 80%, preferably greater than about 90% and more preferably greater than about 95%, when the boron and carbon films are formed on 3-D structures having aspect ratios of about 20:1 or greater, about 40:1 or greater, or about 80:1 or greater. For example, one or more boron and carbon films formed according to one or more processes described herein may demonstrate a conformality performance of greater than about 95% when deposited on high aspect ratio features of a 3-D substrate surface, including aspect ratios of up to about 250:1, including about 150:1 and about 100:1.

As described herein, a boron and carbon (B, C) film can be used in some embodiments as a sacrificial film in a semiconductor device fabrication process. For example, the boron and carbon film may be selectively removed in an etch process. In some embodiments, a boron and carbon film may form a part of a finished semiconductor device. For example, the boron and carbon film may be more resistant to etch than one or more other materials used in the fabrication of the semiconductor device. In some embodiments, the boron and carbon film may be etched by a dry etch process and/or a wet etch process. In some embodiments, a sacrificial boron and carbon film can be selectively removed during fabrication of a semiconductor device using an etch process comprising chlorine (Cl) and/or fluorine (F), such as chlorine and/or fluorine containing plasma processes. In some embodiments, the boron and carbon films can be more resistant to one or more etchants, including wet etchants such as dilute HF solutions.

In some embodiments, the boron and carbon film can demonstrate a desired wet etch selectivity, such as a wet etch selectivity with respect to a thermal silicon oxide (TOX) layer. For example, the boron an carbon film may be more resistant to wet etch than the thermal silicon oxide layer, having a ratio of a wet etch rate of the boron an carbon film to a wet etch rate of a thermal silicon oxide layer less than about 1 (e.g., in dilute HF solution), less than about 0.5, or less than about 0.3. In some embodiments, the ratio of a wet etch rate of the boron and carbon film to a wet etch rate of the thermal silicon oxide layer can be less than about 0.1. In some embodiments, the ratio of a wet etch rate of the boron and carbon film to a wet etch rate of the thermal silicon oxide layer can be less than about 0.05.

In some embodiments, the boron and carbon film can advantageously demonstrate desirable wet etch rates, including etch rates in dilute HF solution. For example, the boron and carbon film can advantageously demonstrate etch rates of less than about 0.2 nanometers per minute (nm/min), including preferably less than about 0.1 nm/min, more preferably less than about 0.05 nm/min, and most preferably less than about 0.02 nm/min. As will be described in further details below, ultrathin boron and carbon materials deposited according to one or more processes described herein may advantageously demonstrate desired resistance to wet etchants, such as dilute HF. In some embodiments, ultrathin boron and carbon films can be resistant or substantially resistant to dilute HF for more than about 30 seconds, preferably more than about 60 seconds, or more preferably more than about 120 seconds. In some embodiments, ultrathin boron and carbon films can be resistant or substantially resistant to dilute HF exposure for up to about 5 minutes, or up to about 10 minutes. For example, ultrathin boron and carbon films may demonstrate etch rates of less than about 0.1 nm/min, less than about 0.05 nm/min, or less than about 0.02 nm/min when exposed to dilute HF for at least the indicated times. In some embodiments, ultrathin boron and carbon films can be resistant or substantially resistant to dilute HF exposure for longer than 10 minutes.

In some embodiments, the boron and carbon film can demonstrate wet etch rates of less than about 0.2 nm/min, including preferably less than about 0.1 nm/min, more preferably less than about 0.05 nm/min, and most preferably less than about 0.02 nm/min in the following wet etchant solutions and at the specified temperatures: phosphoric acid (H₃PO₄) solution at a concentration of about 85 weight % at about room temperature (e.g., a temperature of about 25° C.), a concentrated nitric acid HNO₃ solution (e.g., a solution having a HNO₃ concentration of about 65 to about 75 weight %) at about 80° C., a 5.5 weight % hydrofluoric acid (HF) at about room temperature (e.g., a temperature of about 25° C.), a solution having a ratio of nitric acid:hydrofluoric acid:water (HNO₃:HF:H₂O) at about 1:1:5 at about room temperature (e.g., a temperature of about 25° C.), an aqueous solution of sodium hydroxide (NaOH) having a concentration of NaOH of about 10 weight % at about room temperature (e.g., a temperature of about 25° C.), a concentrated hydrochloric acid (HCl) solution (e.g., a solution having an HCl concentration of about 35 to about 40 weight %) at about room temperature (e.g., a temperature of about 25° C.), and a concentrated sulfuric acid solution (H₂SO₄) (e.g., a solution have a H₂SO₄ concentration of greater than about 90 weight %) at about room temperature (e.g., a temperature of about 25° C.).

In some embodiments, the boron and carbon film may be selectively removed. In some embodiments, the boron and carbon film can have a etch selectivity (e.g., a dry etch and/or a wet etch selectivity) with respect to another material, such as a film of a different composition, in the device of about 5 or greater, including a selectivity of about 10 or greater, about 20 or greater, or about 50 or greater.

In some embodiments, a portion of a boron and carbon film deposited on a sidewall of a three-dimensional structure can demonstrate a desired etch rate, for example, as compared to an etch rate of a portion of the film deposited on a top surface of the three-dimensional feature. In some embodiments, a portion of a boron and carbon film deposited on a sidewall of a three-dimensional structure can demonstrate a uniform or substantially uniform etch rate as a portion of the boron and carbon film deposited on a top surface of the structure. For example, a ratio of an etch rate of a sidewall portion of the boron and carbon film to an etch rate of a top surface portion of the boron and carbon film can be less than about 4, including less than about 2, about 1.5. In some embodiments, the ratio is about 1. In some embodiments, a uniformity of a top surface portion and a sidewall portion of the boron and carbon film can be maintained after being exposed to one or more plasma processes, such as a plasma post-deposition treatment process as described herein.

One or more process parameters for boron and carbon (B, C) film growth process may be adjusted to achieve a desired boron and carbon film characteristic. For example, selection of a boron reactant, a duration of a reactant pulse, a duration of a purge step, a process temperature, and/or a number of repetitions of the reactant pulse, may be determined to provide a boron and carbon film comprising desirable characteristics. In some embodiments, one or more parameters of one cycle of a reactant pulse and purge step can be different from that of another cycle (e.g., one cycle of the reactant pulse and purge step as described with reference to FIG. 1). In some embodiments, a boron reactant can have a B—C bond. In some embodiments, a boron reactant comprises at least one organic ligand, such as a hydrocarbon ligand, including a boron reactant comprising an alkyl group.

As described herein, one or more processes described herein may be used to form an ultrathin boron and carbon film on the substrate, where the boron and carbon films have a thickness in the sub-nanometer range. In some embodiments, the ultrathin boron and carbon film can have a thickness less than about 30 angstroms (Å), less than about 20 Å, less than about 15 Å, less than about 10 Å or less than about 7 Å. In some embodiments, the ultrathin boron and carbon film can have a thickness less than about 5 Å. In some embodiments, the ultrathin boron and carbon film can have a thickness of less than about 3 Å, such as about 1 Å.

In some embodiments, although referred to herein as a film, the ultrathin boron and carbon film may not form a continuous layer on the substrate. For example, the ultrathin boron and carbon film may not fully cover all surfaces of the substrate material on which the ultrathin boron and carbon film is formed. In some embodiments, the ultrathin boron and carbon film may comprise pinholes. As used herein, a thickness of the ultrathin boron and carbon film refers to an average thickness of the film. In some embodiments, the ultrathin boron and carbon film may form a continuous layer on the substrate.

In some embodiments, the ultrathin boron and carbon film may be formed according to one or more cyclic processes described herein, such as a cyclic pulsed CVD processes described herein. In some embodiments, the ultrathin boron and carbon film may be deposited by a pulsed thermal CVD process. For example, a cycle of a pulsed CVD process for forming the ultrathin boron and carbon film may include exposing the substrate to one or more boron precursors for a duration, followed by an interval during which the substrate is not exposed to the boron precursors (e.g., by removing the substrate to an environment free or substantially free of the precursors, and/or by performing purge step). As described herein, supply of the one or more boron precursors into the reaction space may be accompanied by a carrier gas. In some embodiments, the ultrathin boron and carbon film may be formed by performing about 1 to about 100 cycles, preferably about 2 to about 50 cycles, and more preferably about 3 to about 20 cycles. In some embodiments, the ultrathin boron and carbon film may be formed using about 5 to about 10 cycles.

In some embodiments, a deposition rate per cycle of the ultrathin boron and carbon film can depend on a composition of the material on which the ultrathin boron and carbon material is deposited. For example, on a deposition rate on an aluminum nitride (AlN) substrate of an ultrathin boron and carbon film process may be lower than that of a similar or same ultrathin boron and carbon deposition process when depositing on a silicon nitride (SiN) substrate.

In some embodiments, a process for forming the ultrathin boron and carbon film may include continuously or substantially continuously flowing one or more boron precursors during the deposition process. For example, the process may comprise a continuous flow thermal CVD process. In some embodiments, a continuous flow process may provide a shorter process than a process comprising multiple pulses of a reactant (e.g., due to elimination of purge steps). In some embodiments, a continuous flow process may provide improved uniformity relative to a pulsed process. In some embodiments, continuous flow can be selected to provide desired accuracy in control of precursor dose and/or precursor concentration in the reaction space. In some embodiments, continuous flow can be selected based on a configuration of the reactor chamber. For example, a continuous flow process may be selected for a reactor chamber having relatively larger reaction space volume. In some embodiments a continuous flow process may be selected for a batch reactor. In some embodiments, a continuous flow process may be selected for a reactor chamber having relatively higher accuracy in dose control. For example, a continuous flow process may be selected for a particular CVD reaction chamber.

In some embodiments, the ultrathin boron and carbon material may be formed in a single wafer reactor. In some embodiments, the ultrathin boron and carbon film may be formed in a batch reactor. For example, a deposition process for forming the ultrathin boron and carbon film may be performed in a vertical batch reactor. For example, the batch reactor may be configured to process a wafer load of about 25 wafers to about 200 wafers, preferably about 50 wafers to about 150 wafers.

As mentioned above, in some embodiments a process temperature for depositing the ultrathin boron and carbon film in a batch reactor can be about 250° C. to about 400° C., preferably from about 275° C. to about 375° C., and more preferably about 300° C. to about 350° C.

In some embodiments, an ultrathin boron and carbon film can demonstrate a 1 sigma (1σ) non-uniformity of less than about 5%, preferably less than about 2%. For example, an ultrathin boron and carbon film deposited on a 300 millimeter (mm) wafer using one or more processes described herein may demonstrate a 1 sigma non-uniformity of less than about 2%. In some embodiments, relatively lower process temperatures can be used to achieve relatively lower uniformity performances.

In some embodiments, an ultrathin boron and carbon film can be used to enhance the etch selectivity performance of a structure comprising the ultrathin boron and carbon film and another different material. For example, the other material may comprise a material having relatively less resistance to certain etchants, including certain wet etchants, such as dilute HF. Use of the ultrathin boron and carbon film together with the other different material may advantageously facilitate formation of a resulting structure having desired etch properties as well as desired properties of the other different material. For example, ultrathin boron and carbon film can be used with aluminum nitride and/or aluminum oxide to provide a finished structure having desired etch characteristics while providing a structure demonstrating desired electrical and/or optical properties.

In some embodiments, the other material can comprise one or more of a nitride, carbide, oxide, and/or mixtures thereof. In some embodiments, the other material can comprise one or more of a nitride, a carbide, and/or an oxide of a metal and/or a semimetal. In some embodiments, the other material can comprise one or more of a nitride of a metal and/or a semimetal. For example, the one or more nitrides may include silicon nitride, germanium nitride, and/or aluminum nitride. In some embodiments, the other material can comprise one or more of a carbide of a metal and/or a semimetal. In some embodiments, the other material can comprise one or more of an oxide of a metal and/or a semimetal. For example, the one or more oxides may include germanium oxide, and/or silicon oxide.

In some embodiments, the other material may be formed using an ALD and/or CVD process, including plasma enhanced ALD and/or CVD processes. In some embodiments, the other material can preferably be formed using an ALD process, and more preferably using a low-temperature ALD process (e.g., process temperatures of up to about 400° C.). In some embodiments, the other material may be formed in a same tool as the ultrathin boron and carbon material (e.g., cluster tool). For example, the reaction chamber used for depositing the ultrathin boron and carbon material may be on the same cluster tool as the reaction chamber used to deposit the other material, such that transfer between the reaction chambers can be performed without exposing the substrate to ambient air (e.g., “in-situ”). In some embodiments, the same reaction chamber can be used for depositing both the ultrathin boron and carbon material and the other material, and the substrate is not exposed to ambient air between depositing the ultrathin boron and carbon material and the other material.

In some embodiments, the other material can be deposited first and the ultrathin boron and carbon film can be deposited on the other material. For example, the other material may be a substrate on which the ultrathin boron and carbon film is deposited. For example, the ultrathin boron and carbon film can serve as a cap layer for the other material. In some embodiments, the ultrathin boron and carbon film can be deposited first and the other material deposited on the ultrathin boron and carbon film. For example, the ultrathin boron and carbon film can serve as an etch stop layer for the other material. Use of the ultrathin boron and carbon film as a cap layer and/or an etch stop layer with the other material can facilitate tuning of etch properties of the resulting structure.

In some embodiments, an ultrathin boron and carbon film having a thickness of less than about 30 Å, about 20 Å, about 15 Å, about 10 Å, about 7 Å, about 5 Å, or about 3 Å, may be resistant or substantially resistant to removal by dilute HF. Ultrathin boron and carbon films having such thicknesses may serve as an etch stop layer for another material deposited over the ultrathin boron and carbon film, and/or as a cap layer for another material over which the ultrathin boron and carbon film is deposited. In some embodiments, an ultrathin boron and carbon material deposited using about 1 to about 100 deposition cycles, including up to about 50 cycles, about 20 cycles, or about 10 cycles, may demonstrate resistance or substantial resistance to etch by dilute HF. Ultrathin boron and carbon films deposited using less than about 100 deposition cycles may serve as an etch stop layer for another material deposited over the ultrathin boron and carbon film, and/or as a cap layer for another material over which the ultrathin boron and carbon film is deposited.

As described herein, in some embodiments, a boron and carbon film (B, C) can serve as a dopant film, such as a solid state diffusion (SSD) layer. In some embodiments where the boron and carbon film serves as a dopant film, a cap layer is not required over the boron and carbon film. In some embodiments a boron and carbon film (B, C) can itself serve as a cap layer over a different SSD layer, for doping a substrate. A boron and carbon dopant film may be formed according to one or more processes described herein. For example, a process for depositing a boron and carbon solid state diffusion layer and/or a boron and carbon cap layer may comprise a pulsed thermal CVD process. In some embodiments, the thermal CVD process may include contacting a surface on which the boron and carbon film is deposited with one or more reactant pulses comprising one or more boron reactants described herein. For example, a reactant pulse may include a boron reactant comprising a B—C bond, including a boron reactant comprising an organic ligand, such as a trialkylboron (e.g., triethylboron (B(C₂H₅)₃), TEB, and/or trimethylboron (B(CH₃)₃), TMB). In some embodiments, the reactant pulse comprises a carrier gas, such as argon gas. For example, a cycle of a thermal CVD process for depositing the boron and carbon solid state diffusion layer and/or boron and carbon cap layer may include a reactant pulse comprising TEB and argon gas, where the reactant pulse is followed by a purge step comprising flow of argon gas and in which flow of the TEB is not flowed, such that flow of argon gas is continued throughout the cycle while TEB is flowed only during a portion of the cycle. In some embodiments, the cycle may be repeated up to about 1,000 times, about 1,500 times, about 2,000 times, or about 5,000. In some embodiments, the cycle can be repeated about 2 to about 1,000 times, including about 2 to about 2,000 times, about 3 to about 2,000 times, or about 5 to about 5,000 times. In some embodiments, the cycle can be repeated from about 10 to about 1000 times. In some embodiments, the cycle can be repeated about 50 to about 2,000 times. In some embodiments, the cycle can be repeated about 100 to about 1,500 times.

In some embodiments, the reactant pulse can have a duration of about 0.1 seconds (s) to about 5 s, including about 0.1 s to about 1 s. For example, a reactant pulse can have a duration of about 0.3 s. In some embodiments, the purge step can have a duration of about 0.5 s to about 10 s, including from about 0.5 s to about 5 s. For example, the purge step may have a duration of about 1 s.

In some embodiments, processes for depositing the boron and carbon solid state diffusion layer and/or boron and carbon cap layer can be performed at process temperatures of about 300° C. to about 450° C., including about 350° C. to about 450° C., or about 400° C. to about 450° C. For example, the boron and carbon solid state diffusion layer and/or boron and carbon cap layer may be deposited at a temperature of about 430° C. In some embodiments, the boron and carbon solid state diffusion layer and/or boron and carbon cap layer can be deposited at a reactor chamber pressure of about 0.5 Torr to about 10 Torr, for example about 6 Torr.

In some embodiments, a boron and carbon film thickness can be selected to provide desired doping on the underlying substrate. For example, a thickness of a boron and carbon solid state diffusion layer and/or a boron and carbon cap layer may be selected to achieve desired substrate doping. In some embodiments, a boron and carbon solid state diffusion layer can have a thickness of up to about 5 nanometers (nm). In some embodiments, the boron and carbon solid state diffusion layer can have a thickness of about 4 nm, or about 3 nm. For example, the boron and carbon solid state diffusion layer may have a thickness of about 1 nm. In some embodiments, a film stack comprising a boron and carbon solid state diffusion layer over a substrate without or substantially without a cap layer may have a thickness less than about 4 nm. In some embodiments, a boron and carbon cap layer can have a thickness of up to about 5 nm, including up to about 4 nm, or about 3 nm. For example, the boron and carbon cap layer can have a thickness of about 1 nm. In some embodiments, a film stack comprising a 1 nm thick boron and carbon solid state diffusion layer over a substrate without or substantially without a cap layer, or a film stack comprising a 1 nm thick boron and carbon cap layer over a conventional boron-containing solid state diffusion layer may provide desired doping of an underlying substrate. In some embodiments, a film stack having a thickness up to about 4 nm and comprising a boron and carbon solid state diffusion layer over a substrate without or substantially without a cap layer, or a film stack having a thickness up to about 4 nm and comprising a boron and carbon cap layer over a conventional boron-containing solid state diffusion layer, may provide desired doping of an underlying substrate.

One or more process parameters for boron and carbon dopant film growth process may be adjusted to achieve a desired boron and carbon dopant film characteristic, such as to provide a desired boron concentration in the dopant film to achieve desired doping of an underlying substrate. One or more process parameters for boron and carbon dopant film growth process may be adjusted to achieve a desired boron and carbon film thickness so as to provide desired doping of the underling substrate. For example, selection of a boron reactant, a duration of a reactant pulse, a duration of a purge step, a process temperature, and/or a number of repetitions of the reactant pulse, may be determined to provide a boron and carbon film comprising desirable characteristics, such as desired boron and carbon film thickness. In some embodiments, one or more parameters of one cycle of a reactant pulse and purge step can be different from that of another cycle (e.g., one cycle of the reactant pulse and purge step as described with reference to FIG. 1) in order to deposit a film with desired characteristics.

In some embodiments, a thermal anneal process is conducted after depositing the boron and carbon film dopant film. For example, the thermal anneal process can be performed after a desired film stack for a solid state doping scheme has been formed (e.g., a film stack comprising a boron and carbon solid state diffusion layer or a film stack comprising a boron and carbon cap layer). The thermal anneal process drives the boron dopant into the underlying substrate, and can be conducted under process temperatures of about 800° C. to about 1500° C., including about 800° C. to about 1200° C. In some embodiments, the anneal process can be performed in an atmosphere comprising nitrogen gas (N₂) and/or helium gas (He). In some embodiments, the thermal anneal process may include hydrogen gas (H₂). In some embodiments, a hydrogen gas (H₂) containing atmosphere may provide increased diffusion of boron into the substrate, such as compared to a thermal anneal process without using the hydrogen gas (H₂). In some embodiments, the thermal anneal process can have a duration of about 0.5 s to about 5 s, including about 0.5 s to about 3 s. For example, a thermal anneal process may be performed at a process temperature of about 1000° C. in nitrogen-containing atmosphere (e.g., N₂ atmosphere) for about 1 s. The thermal anneal process may be performed a number of times to achieve desired boron dopant profile within the underlying substrate. For example, the thermal anneal process may be performed once to achieve desired dopant profile. For example, the thermal anneal process may be performed twice to achieve the desired dopant profile.

FIGS. 2A and 2B show examples of film stacks comprising boron and carbon (B, C) films. FIG. 2A shows a boron and carbon dopant film deposited directly on a silicon substrate. For example, the boron and carbon film may be a solid state diffusion (SSD) layer deposited directly onto the silicon substrate such that subjecting the boron and carbon film to a thermal anneal process can drive boron from the boron and carbon film into the silicon substrate, providing dopant for the substrate.

In some embodiments, an un-doped layer can be formed on the substrate and the boron and carbon solid state diffusion layer can be formed on the un-doped layer. In some embodiments, the un-doped layer can comprise silicon oxide. For example, a boron and carbon solid state diffusion layer may be deposited on a silicon oxide layer that was formed on a silicon substrate. Without being limited by any particular theory or mode of operation, the un-doped layer may facilitate control of the substrate doping. For example, formation of the un-doped silicon oxide layer on the substrate such that the boron and carbon solid state diffusion layer is not directly deposited on the substrate may provide desired boron concentration profile in the substrate after anneal. In some embodiments, the un-doped layer may have a thickness of about 0.5 nanometers (nm) to about 4 nm, including about 0.5 nm to about 3 nm, about 0.5 nm to about 2 nm, or about 0.5 nm to about 1 nm. For example, in some embodiments an un-doped silicon oxide layer may have a thickness of about 0.5 nm to about 4 nm.

As described herein, a boron and carbon film can serve as a cap layer in solid state doping. For example, a conventional dopant film can be formed over a substrate and a boron and carbon cap layer can be formed over the conventional dopant film. In some embodiments, the conventional dopant film can be a boron doped film. FIG. 2B shows a first boron doped film on a silicon substrate, and a second, different boron and carbon film on the boron doped film. The first boron doped film may comprise a conventionally formed boron-containing solid state diffusion layer, such as a BSG layer. The second boron and carbon film on the conventionally formed boron doped film may be a cap layer. In some embodiments the cap layer suppresses out-diffusion of dopant from the underlying boron doped film. For example, the first boron doped film can be formed directly on the silicon substrate and the second boron and carbon cap layer can be deposited directly on the boron doped film by a process as described herein. In some embodiments, the boron and carbon cap layer can be deposited on the boron doped film without or substantially without being exposed to ambient air (e.g., without an air exposure between the processes for depositing the boron doped film and the boron and carbon cap layer). For example, the boron and carbon cap layer can be deposited on the boron doped film in an in-situ sequential deposition process. The film stack shown in FIG. 2B may be subjected to a thermal anneal process to drive boron from the boron doped film and/or boron and carbon cap layer into the silicon substrate.

FIG. 3 shows a flow chart 200 of another example of a process for forming boron and carbon (B, C) films, according to some embodiments. In block 202, the substrate is exposed to a boron and carbon film growth process. The boron and carbon film growth process may comprise a deposition process, such as a pulsed thermal CVD process, for depositing a boron and carbon film of a desired thickness and/or composition. For example, the boron and carbon film growth process may comprise repeating a number of times a cycle comprising a reactant pulse followed by a purge step (e.g., the reactant pulse and purge step as described with reference to FIG. 1). The cycle may be repeated a number of times to achieve a desired boron and carbon film thickness and/or composition.

In block 204, a post-deposition treatment process can be carried out on the deposited boron and carbon film. In some embodiments, the post-deposition treatment process comprises a plasma process. For example, the treatment process may comprise contacting the deposited boron and carbon film with one or more energized species for a duration of time. In some embodiments, the post-deposition treatment process comprises contacting the substrate comprising the boron and carbon film with a plasma. For example, the substrate can be contacted with a plasma generated using nitrogen-containing compounds (e.g., nitrogen gas), a noble gas, and/or oxygen-containing compounds (e.g., oxygen gas and/or ozone). In some embodiments, the post-deposition treatment process can be followed by a purge step. For example, the purge step may include flow of nitrogen gas and/or one or more noble gases. In some embodiments, purging the reactor chamber subsequent to the post-deposition treatment process can include turning off the plasma power while continuing to flow one or more of the gases used to generate the plasma for the post-deposition treatment process. For example, during the purge step the one or more gases used in generating the plasma for the post-deposition treatment process may continue to be flowed into the reactor while the plasma power is turned off, the flow rate of the one or more gases during the purge step being the same as or different from that during the post-deposition treatment process.

In some embodiments, exposing a boron and carbon film to a plasma post-deposition treatment process can facilitate a further reduced etch rate of the treated boron and carbon film, for example as compared to that of a boron and carbon film formed without performing the post-deposition treatment process. Without being limited by any particular theory or mode of operation, exposing a boron and carbon film to a plasma post-deposition treatment process as described herein may increase the density of the boron and carbon film, thereby providing a treated boron and carbon film exhibiting decreased etch rate as compared to an untreated boron and carbon film. In some embodiments, the etch rate of a portion of the boron and carbon film deposited on a sidewall of a three-dimensional structure can demonstrate a uniform or substantially uniform etch rate as a portion of the boron and carbon film deposited on a top surface of the structure subsequent to exposure of the boron and carbon film to a plasma post-deposition treatment process (e.g., etch rate uniformity between a top portion and a sidewall portion of the boron and carbon film can be maintained subsequent to exposure to a plasma process of the post-deposition treatment process, such as compared to that of the film prior to the post-deposition treatment process). For example, a ratio of an etch rate of a sidewall portion of the boron and carbon film to an etch rate of a top surface portion of the boron and carbon film subsequent to a plasma post-deposition treatment process can be less than about 4, including less than about 2, about 1.5. In some embodiments, the ratio is about 1.

As described herein, in some embodiments, a plasma post-deposition treatment process may comprise contacting a deposited boron and carbon film with a nitrogen-containing plasma (e.g., contacting the deposited boron and carbon film with nitrogen-containing radicals and/or ions). One or more nitrogen-containing compounds may be used to generate the nitrogen-containing plasma, such as nitrogen-containing compounds which do not have hydrogen (H). For example, the plasma post-deposition treatment process may comprise energetic species generated using nitrogen gas (N₂).

In some embodiments, the plasma post-deposition treatment process comprises exposing the boron and carbon film to the nitrogen-containing plasma for a duration of about 1 to about 500 seconds (s), 10 s to about 300 s, including about 10 s to about 100 s, or about 10 s to about 50 s. The nitrogen-containing plasma post-deposition treatment process may be performed at a process temperature of about 100° C. to about 500° C., including about 200° C. to about 500° C., and about 200° C. to about 400° C., and a pressure of about 0.1 Torr to about 20 Torr, including about 1 Torr to about 10 Torr, and about 1 Torr to about 8 Torr. In some embodiments, a plasma power for generating the nitrogen-containing plasma can be about 50 Watts (W) to about 2000 W, including about 50 W to about 1000 W, about 100 W to about 400 W, and about 200 W to about 400 W.

In some embodiments, a plasma post-deposition treatment process comprises contacting a deposited boron and carbon film with a noble gas-containing plasma (e.g., contacting the deposited boron and carbon film with noble gas-containing radicals and/or ions). For example, the plasma post-deposition treatment process may comprise a plasma comprising energetic species generated using helium (He) gas, argon gas (Ar) and/or neon (Ne) gas. In some embodiments, the plasma post-deposition treatment process comprises exposing the boron and carbon film to the noble gas-containing plasma for a duration of about 10 seconds (s) to about 300 s, including about 10 s to about 100 s. The noble gas-containing plasma post-deposition treatment process may be performed at a process temperature of about 100° C. to about 500° C., including about 200° C. to about 500° C., and about 200° C. to about 400° C., and a pressure of about 0.1 Torr to about 20 Torr, including about 1 Torr to about 10 Torr, and about 1 Torr to about 8 Torr. In some embodiments, a plasma power for generating the noble gas-containing plasma can be about 50 Watts (W) to about 2000 W, including about 50 W to about 1000 W, about 100 W to about 400 W, and about 200 W to about 400 W.

In some embodiments, the plasma post-deposition treatment process comprises contacting a deposited boron and carbon film with an oxygen-containing (O) plasma (e.g., contacting the deposited boron and carbon film with oxygen-containing radicals and/or ions). In some embodiments, the oxygen-containing plasma can be generated using oxygen-containing compounds, such as oxygen gas (O₂) and/or ozone (O₃). In some embodiments, the plasma post-deposition treatment process may comprise exposing the boron and carbon film to the oxygen-containing plasma for a duration of about 10 seconds (s) to about 300 s, including about 10 s to about 100 s. The oxygen-containing plasma post-deposition treatment process may be performed at a process temperature of about 100° C. to about 500° C., including about 200° C. to about 500° C., and about 200° C. to about 400° C., and a pressure of about 0.1 Torr to about 20 Torr, including about 1 Torr to about 10 Torr, and about 1 Torr to about 8 Torr. In some embodiments, a plasma power for generating the oxygen-containing plasma can be about 50 Watts (W) to about 2000 W, including about 50 W to about 1000 W, about 100 W to about 400 W, and about 200 W to about 400 W.

In some embodiments, the oxygen-containing plasma (e.g., generated using oxygen gas and/or ozone) post-deposition treatment process can increase a refractive index of the boron and carbon film. In some embodiments, the oxygen-containing plasma post-deposition treatment process can reduce a thickness of the boron and carbon film (e.g., a thickness of the treated film can be less than a thickness of the film prior to being exposed to the post-deposition treatment process). Without being limited by any particular theory or mode of operation, exposing a boron and carbon film to an oxygen-containing plasma may facilitate replacement of hydrogen (H) and/or carbon (C) components of the film with oxygen (O), for example generating a BO_(x) containing film. Further without being limited by any particular theory or mode of operation, a change in composition of the boron and carbon film, such as the replacement of hydrogen (H) and/or carbon (C) components of the film with oxygen (O), may be reflected by a decrease in a refractive index of the film, and/or a decrease in film thickness (e.g., due to an increased film density and/or removal of volatile BO_(x) species). For example, exposure of the boron and carbon film to an oxygen-containing plasma under certain conditions may result in complete or substantially complete removal of the deposited boron and carbon film (e.g., a plasma etch of the boron and carbon film).

In some embodiments, a plasma post-deposition treatment process can be performed once subsequent to depositing a boron and carbon film of a desired thickness and/or composition. In some embodiments, a plasma post-deposition treatment process can be carried out at intervals after every repetition of a number of cycles of a deposition process for depositing the boron and carbon film (e.g., after a number of repetitions of a cycle of the reactant pulse and purge step as described with reference to FIG. 1). For example, a plasma post-deposition treatment process may be performed after every 1, 2, 5, 10, 100, 1,000 cycles of a boron and carbon film deposition process. Other numbers of cycles may also be suitable. In some embodiments, a ratio of a number of cycles of a process for depositing a boron and carbon film (e.g., a ratio of Y:X) to a number of cycles of the plasma post-deposition treatment process for forming a boron and carbon film having desired characteristics can be about 5,000:1 to about 1:1, including about 2,000:1 to about 50:1. In some embodiments, the ratio of the number of cycles for the process of depositing a boron and carbon film to the number of cycles of the plasma post-deposition treatment process can be about 1,500:1 to about 1:1, including about 1,000:1 to about 1:1, about 500:1 to about 1:1, about 100:1 to about 1:1, about 50:1 to about 1:1, and about 20:1 to about 1:1.

In some embodiments, one or more parameters of the plasma post-deposition treatment process may be adjusted to facilitate formation of a boron and carbon film having desirable characteristics. For example, a duration, plasma power, pressure, plasma composition and/or the number of repetitions of the process, may be selected to facilitate producing a boron and carbon film having desired etch characteristics.

A suitable reaction chamber for one or more boron and carbon (B, C) film deposition processes described herein may be part of a cluster tool in which a variety of different processes in the formation of an integrated circuit are carried out. In some embodiments, one or more boron and carbon film deposition processes described herein can be performed in a batch reactor, including for example in a mini-batch reactor (e.g., a reactor having a capacity of eight substrates or less) and/or a furnace batch reactor (e.g., a reactor having a capacitor of fifty or more substrates). In some embodiments, one or more boron and carbon film deposition processes described herein can be performed in a single wafer reactor. In some embodiments, a spatial reactor chamber may be suitable. In some embodiments, a reactor chamber having a cross-flow configuration can be suitable (e.g., a reactor chamber configured to provide gas flow parallel or substantially parallel to a substrate surface positioned in the reactor chamber). In some embodiments, a reactor chamber having a showerhead configuration can be suitable (e.g., a reactor chamber configured to provide gas flow perpendicular or substantially perpendicular to a substrate surface positioned in the reactor chamber).

In some embodiments, boron and carbon films which serve as dopant films are not subjected to a plasma post-deposition treatment process. For example, boron and carbon dopant films may not be subjected to one or more plasma post-deposition treatment processes described herein prior to subsequent processing, such as prior to a thermal anneal process for driving dopant into the underlying substrate.

Exemplary single wafer reactors are commercially available from ASM America, Inc. (Phoenix, Ariz.) under the tradenames Pulsar® 2000 and Pulsar® 3000 and ASM Japan K.K (Tokyo, Japan) under the tradename Eagle® XP and XP8. Exemplary batch ALD reactors are commercially available from and ASM Europe B.V (Almere, Netherlands) under the tradenames A400™ and A412™.

Examples of B, C Films

FIG. 4 is a graph of the growth rates of boron and carbon (B, C) films deposited according to some embodiments, in angstroms per cycle (Å/cycle), versus process temperature, in degrees Celsius. The boron and carbon films (B, C) of FIG. 4 were deposited using a pulsed thermal CVD process in a Pulsar® 3000 reactor chamber having a cross-flow configuration. One cycle of the pulsed thermal CVD process included a reactant pulse having a duration of about 0.5 s followed by a purge step having a duration of about 5 s. The reactant pulse included supplying TEB and nitrogen gas into the reactor chamber. The TEB was supplied into the reactor chamber using a vapor draw method by providing vaporized TEB from a source container maintained at a temperature of about 20° C. The pressure of the reactor chamber during the reactant pulse was maintained at about 0.1 Torr to about 10 Torr. The purge step included flowing of nitrogen gas through the reactor chamber. Growth rates of boron and carbon films deposited according to the pulsed thermal CVD process were measured at process temperatures of about 375° C., about 400° C. and about 450° C. As shown in FIG. 4, the growth rate of the boron and carbon film per cycle increased with increasing process temperature. As shown in FIG. 4, a boron and carbon film deposited using such a pulsed thermal CVD process can have a linear or substantially linear relationship with the process temperature.

Composition of boron and carbon (B, C) films deposited according to the process described with reference to FIG. 4 at a process temperature of about 400° C. was measured by rutherford backscattering spectrometry (RBS), and was found to have a boron and carbon stoichiometry of about B_(0.608)C_(0.392), or B_(1.5)C. The refractive index of boron and carbon films deposited according to the process described with reference to FIG. 4 at a process temperature of about 400° C. was measured by spectroscopic ellipsometry. The refractive index was found to be about 1.98 at a wavelength of about 633 nanometers (nm). Wet etch rate performance in dilute hydrofluoric acid solution (e.g., 0.5 weight % aqueous HF solution) of films deposited according to the process described with reference to FIG. 4 at a process temperature of about 400° C. were measured and was found to be surprisingly resistant to the dilute HF solution. It was found that the wet etch rate in dilute HF solution was negligible, for example after up to about 10 minutes exposure to the dilute HF solution (e.g., a dHF dip of up to about 10 minutes). In some embodiments a negligible etch rate is observed up to about a 30 minute exposure or longer. It was found that the wet etch rate of these films in dilute hydrofluoric acid solution is less than 0.3× that of thermal silicon oxide (TOX).

FIG. 5 shows fourier transform infrared spectroscopy (FTIR) analysis of boron and carbon (B, C) films deposited according to the process described with reference to FIG. 4 at a process temperature of about 400° C. The FTIR analysis shows presence of C—H, B—H, B—C, B—B and C—C bonds in the boron and carbon films. For example, the peak at about 2902 cm⁻¹ can be attributed to C—H bonds, and the peak at about 2573 cm⁻¹ can be attributed to B—H bonds in the film. The peaks at 1201 cm⁻¹ and 1051 cm⁻¹ indicate presence of B—C, B—B and C—C bonds.

Boron and carbon (B, C) films were deposited on blanket wafers having a diameter of about 300 millimeters (mm) upon using the process as described with reference to FIG. 4 at a process temperature of about 400° C. The deposition was performed in a Pulsar® 3000 reactor chamber having a cross-flow configuration. A mean film thickness was measured at about 35.58 nm after application of 1,000 cycles of the pulsed thermal CVD process of FIG. 4. The deposited boron and carbon film showed increased thickness toward the center of the wafer, for example as compared to the edge of the wafer, such as the leading edge of the wafer (e.g., a portion of the wafer edge further away from the wafer notch). Without being limited by any particular theory or mode of operation, such a thickness profile may indicate a surface reaction limited growth mechanism, and the thickness variations may be due to temperature variations of the susceptor on which the wafer was positioned. A surface reaction limited growth can advantageously facilitate improved film conformality performance for deposition of boron and carbon films upon 3-D features.

Boron and carbon (B, C) films were deposited on blanket wafers in a Pulsar® 3000 reactor chamber having a cross-flow configuration at a process temperature of about 450° C. The mean thickness of the deposited boron and carbon film was about 81.88 nm after application of 1,000 cycles of the pulsed thermal CVD process of FIG. 4. As compared to the boron and carbon film deposited at about 400° C., the films deposited at about 450° C. demonstrated an increased thickness. The deposited boron and carbon films had an increased thickness closer to the leading edge of the blanket wafer, for example as compared to the boron and carbon films deposited at 400° C. Without being limited by any particular theory or mode of operation, an increased thickness proximate to the leading edge may indicate a mass-transport limited film growth mechanism, versus a surface reaction limited growth mechanism.

FIGS. 6A-6D are scanning electron microscopy (SEM) images showing cross-section views of a boron and carbon (B, C) film deposited on a high aspect ratio trench structure 500 using the deposition process as described with reference to FIG. 4. The boron and carbon film was deposited with a process temperature of about 400° C., in a Pulsar® 3000 reactor chamber, and by applying 1,500 cycles of the reactant pulse followed by the purge step as described with reference to FIG. 4. FIG. 6A shows, at 15 k× magnification, a SEM image of the high aspect ratio trench structure 500. FIG. 6B shows, at 100 k× magnification, a SEM image of an upper portion 502 of the high aspect ratio trench structure 500. FIG. 6C shows, at 100 k× magnification, an SEM image of a mid-section 504 of the high aspect ratio trench structure 500, and FIG. 6D shows, at 100 k× magnification, a SEM image of a lower portion 506 of the high aspect ratio trench structure 500. A thickness of the deposited boron and carbon film in each of the upper, mid and lower portions of the high aspect ratio trench structure are shown in FIGS. 6B, 6C and 6D, respectively. As shown in FIG. 6, a relatively uniform film thickness was achieved on sides of the high aspect ratio trench structure at the upper, mid and lower portions of the trench structure, for example demonstrating the improved conformality of the deposited boron and carbon film. For example, a film thickness of about 72 nm was measured in the upper portion 502 of the high aspect ratio trench structure 500, a film thickness of about 69 nm was measured at a mid-section 504 of the trench structure 500, and a film thickness of about 69 nm was measured at a lower portion 506 of the trench structure 500, for example demonstrating that a conformality of greater than or equal to about 95% was achieved. Without being limited by any particular theory or mode of operation, deposition of the boron and carbon film at a process temperature of about 400° C. or lower may facilitate deposition of the film in a surface reaction limited regime, facilitating improved conformality of the deposited film.

FIG. 7 is a graph showing the removal rate of various boron and carbon (B, C) films when exposed to 0.5 weight % HF solution (dilute HF solution), as a function of the number of deposition cycles used to form the corresponding boron and carbon film. The y-axis shows the thicknesses of the boron and carbons films removed, in angstroms (Å), after exposing the films to dilute HF for about 60 seconds. The x-axis shows the number of deposition cycles used to form the respective boron and carbon films, and the removal rates were measured for boron and carbon films deposited using 1 cycle, 10 cycles, 20 cycles and 30 cycles. Etch performance after exposure to dilute HF for boron and carbon films deposited on four different substrates are shown. Etch performance curve A in FIG. 7 corresponds to boron and carbon films deposited on silicon nitride (SiN) formed using a low process temperature process. Etch performance curve B corresponds to boron and carbon films deposited on native silicon oxide. Etch performance C corresponds to boron and carbon films deposited on aluminum nitride (AlN), where the aluminum nitride was subjected to an air break after formation of the aluminum nitride and prior to the deposition of the boron and carbon film on the aluminum nitride. Etch performance curve D of FIG. 7 corresponds to boron and carbon films deposited on aluminum nitride (AlN), where the aluminum nitride was not subjected to an air break after formation of the aluminum nitride and prior to the deposition of the boron and carbon film on the aluminum nitride.

The boron and carbon films of FIG. 7 were deposited in a batch reactor having a 120-wafer load. The films were deposited by supplying into the reactor chamber the corresponding number of deposition cycles. Each of the cycles of the boron and carbon film deposition process included a boron precursor pulse having a duration of about 5 seconds, where the boron precursor pulse included flow of TEB and nitrogen gas (N₂) into the reactor chamber, the nitrogen gas (N₂) serving as an inert carrier gas. Each cycle was performed at a process temperature of about 350° C., and included a purge step following the boron precursor pulse. The purge step had a duration of about 18 seconds and included flow of nitrogen gas (N₂) into the reactor chamber.

As shown in FIG. 7, the boron and carbon films generally exhibited an increased resistance to removal by dilute HF as the number of deposition cycles used to form the films increased. The boron and carbon film deposited on the low temperature process silicon oxide using 10 deposition cycles and higher demonstrated a resistance to removal by 60 seconds exposure to dilute HF. Meanwhile, the boron and carbon film deposited on the native silicon oxide using 20 deposition cycles and higher demonstrated a resistance to removal by 60 seconds exposure to dilute HF. The boron and carbon film deposited using 20 deposition cycles and higher on the aluminum nitride subjected to an air break demonstrated a resistance to removal by 60 seconds exposure to dilute HF, while 30 deposition cycles were used for depositing the boron and carbon film on the aluminum nitride not subjected to an air break which demonstrated a resistance to removal by 60 seconds exposure to dilute HF.

FIG. 8 is a graph showing deposition rates of boron and carbon (B, C) films as a function of process temperature, where the reactant pulses for the deposition processes included TEB and argon gas. Deposition rates, in nanometers per minute (nm/min), are shown in the y-axis and process temperatures corresponding to each graphed deposition rate, in degrees Celsius, are shown on the x-axis. The boron and carbon films of FIG. 8 were deposited using a pulsed thermal CVD process in an Eagle® 12 reactor. One cycle of the pulsed thermal CVD process included a reactant pulse having a duration of about 0.3 s followed by a purge step having a duration of about 1 s. The reactant pulse included supplying TEB and argon gas into the reactor chamber. The TEB was supplied into the reactor chamber using a vapor draw method by providing vaporized TEB from a source container maintained at a temperature of about 20° C. The pressure of the reactor chamber during the reactant pulse was maintained at about 0.1 Torr to about 10 Torr. The purge step included flowing of argon gas through the reactor chamber. Growth rates of boron and carbon films deposited according to the pulsed thermal CVD process were measured at process temperatures of about 350° C., about 400° C., about 420° C. and about 430° C. As shown in FIG. 8, the growth rate of the boron and carbon film per cycle increased with increasing process temperature. As shown in FIG. 8, a boron and carbon film deposited using such a pulsed thermal CVD process using TEB and argon gas can have a non-linear relationship with the process temperature. For example, the film growth rate at a process temperature of about 430° C. is significantly higher than the film growth at a process temperature of about 350° C. In some embodiments, such boron and carbon films may be dopant films, including boron and carbon solid state diffusion layers and/or cap layers.

FIG. 9A shows a scanning transmission electron microscopy (STEM) image at 180 k× magnification of a cross-section view of a boron and carbon film deposited at a process temperature of about 430° C. using the process described above with reference to FIG. 8. The boron and carbon film demonstrated conformal coverage of the trench feature. As shown in FIG. 9A the boron and carbon film was deposited directly onto a substrate.

FIG. 9B is a table providing the composition of the boron and carbon (B, C) film of FIG. 9A. As shown in the table, the boron and carbon film mainly included boron, carbon and hydrogen. The boron and carbon film included about 35 atomic % boron (B), about 33 atomic % carbon (C), about 28 atomic % hydrogen (H), about 2 atomic % nitrogen (N), and about 2 atomic % oxygen (O).

FIG. 10 is a graph showing boron concentration at various depths in a silicon layer following annealing of a boron and carbon film deposited over the silicon layer by a process described above. The boron concentration was measured using Secondary Ion Mass Spectrometry (SIMS). Boron concentration is shown on the y-axis in atoms per cubic centimeter (atoms/cm³), and depth measured from the top surface of the silicon layer is shown on the x-axis in nanometers (nm). A boron and carbon film having a thickness of about 1 nm was deposited directly on a silicon substrate using the process described with reference with FIG. 8 at a process temperature of about 415° C. The film stack comprising the boron and carbon solid state diffusion layer was subsequently subjected to a thermal anneal process performed at a process temperature of about 1000° C. for a duration of about 1 s in nitrogen (N₂) atmosphere.

As shown in FIG. 10, a boron concentration, or doping level, of about 2E+20 atom/cm³ at the silicon substrate surface was achieved using the 1 nm thick boron and carbon solid state diffusion layer. The boron concentrations achieved using the boron and carbon solid state diffusion layer were significantly higher than boron concentrations obtained using a conventional solid state diffusion layer and conventional cap layer (e.g., a 3 nm silicon dioxide cap layer over a 1 nm borosilicate glass, BSG, solid diffusion layer). For example, boron concentrations achieved using the boron and carbon solid state diffusion layer were significantly higher than boron concentrations obtained using the conventional solid state diffusion layer and conventional cap layer up to depths of about 40 nm.

FIG. 11 is a graph showing an aging analysis of a boron and carbon film using Fourier Transform Infrared Spectroscopy (FTIR). The boron and carbon film was deposited using the process described with reference with FIG. 8 at a process temperature of about 415° C. The FTIR analysis was performed on the boron and carbon film for about seven days after deposition of the film. The boron and carbon film was exposed to ambient air, such as a cleanroom ambient, for the duration of the seven days.

The FTIR analysis of FIG. 11 shows that features of the boron and carbon film remained unchanged or substantially unchanged over the course of about 7 days, demonstrating desired chemical stability after deposition. For example, the FTIR analysis showed that the film did not absorb significant amounts of moisture from the air. A boron and carbon film which can demonstrate desired stability after deposition, for example demonstrating negligible absorption of moisture when exposed to ambient air, can be used as a cap layer in solid state doping schemes. As described herein, a boron and carbon cap layer may be deposited onto a conventional solid state diffusion layer, such as a borosilicate glass (BSG) layer, to provide desired doping of a semiconductor substrate. Without being limited by any particular theory or mode of operation, a boron and carbon film which can demonstrate negligible absorption of moisture when exposed to ambient air can be used as a solid state diffusion layer without or substantially a cap layer.

FIG. 12 is a table showing optical properties and deposition performances of an example of a boron and carbon film deposited using the process described with reference to FIG. 8 at a process temperature of about 415° C. The film was subjected to a thermal anneal at a process temperature of about 1000° C. under nitrogen (N₂) atmosphere for a duration of about 1 s. As shown in the table, the deposition process provided a deposition rate of about 0.045 nanometers/cycle and about 2.091 nanometers/minute. The 1 sigma (1σ) non-uniformity of the deposited film was about 18.42%.

The refractive index of the boron and carbon film was measured by spectroscopic ellipsometry. As shown in the table of FIG. 12, the film demonstrated an average refractive index of about 1.805 at a wavelength of about 633 nanometers (nm).

Boron and Carbon Containing Silicon Nitride Films

As described herein, silicon nitride films can be deposited that include boron and carbon components, and silicon nitride films comprising boron and carbon components can have a wide variety of applications, including applications in semiconductor device fabrication. Deposition of silicon nitride based films having desired characteristics using atomic layer deposition (ALD) at reduced temperatures (e.g., at temperatures of less than about 500° C.), for example to provide processes with reduced thermal budgets, can be difficult. Silicon nitride based films deposited by conventional processes at lower process temperatures may provide films having poor film quality, poor film conformality to three-dimensional (3-D) structures upon which the silicon nitride based film is deposited, undesirably high dry etch rates, and/or undesirably low etch selectivity (e.g., etch selectivity to another material in a semiconductor device, including a thermal silicon oxide material, such that the silicon nitride film may withstand one or more subsequent thermal silicon oxide etch steps used in the device fabrication process).

The formula of a silicon nitride film is generally referred to herein as SiN for convenience and simplicity. However, the skilled artisan will understand that the actual formula of the silicon nitride can be SiNx, where x varies from about 0.5 to about 2.0, as long as some Si−N bonds are formed. In some cases, x preferably varies from about 0.9 to about 1.7, more preferably from about 1.0 to about 1.5, and most preferably from about 1.2 to about 1.4. Generally silicon nitride where Si has an oxidation state of +IV is formed and the amount of nitride in the material might vary.

The formula of a silicon nitride film comprising boron and carbon components is generally referred to herein as SiN(B, C) for convenience and simplicity. However, the skilled artisan will understand that the actual formula of the SiN(B, C) can be SiN_(x)(B_(y), C_(z)). In some embodiments, for example, x can vary from about 0.5 to about 3.0, as long as some Si—N bonds are formed. In some cases, x preferably varies from about 1.0 to about 2.0, and more preferably from about 1.3 to about 1.8. In some embodiments, y can be between about 0.1 to about 5.0, including preferably from about 0.3 to about 3.0, and more preferably from about 0.5 to about 1.5. For example, y can be about 1.5. In some embodiments, z can be from about 0.1 to about 5.0, including preferably from about 0.2 to about 2.5, and more preferably from about 0.3 to about 1.3. For example, z can be about 1.0.

One or more methods described herein can include an atomic layer deposition (ALD) process and/or a chemical vapor deposition (CVD) process and can be used to form a silicon nitride based film, such as a silicon nitride film comprising boron and carbon components SiN(B, C). In some embodiments, the silicon nitride films comprising boron and carbon components have one or more of improved conformal coverage of three-dimensional (3-D) features, a desirable dry etch rate, a desirable wet etch rate, and/or a desirable etch selectivity with respect to another material (e.g., a thermal silicon oxide layer (TOX) in a semiconductor device). For example, a silicon nitride film including boron and carbon components (e.g., for applications such as spacer material of gate features in semiconductor transistors, including multi-gate transistors such as FinFETs) deposited according to one or more processes described herein can demonstrate improved step coverage, reduced etch rate in a wet etchant (e.g., resistance against wet etchant, such as a dilute hydrofluoric acid (HF or dHF) solution, such as a 0.5 weight % HF solution), and/or a reduced wet etch ratio with respect to a thermal silicon oxide material (e.g., a ratio of a wet etch rate of the silicon nitride based film to a wet etch rate of the thermal silicon oxide material of less than about 1, including less than about 0.5). In some embodiments, a silicon nitride film including boron and carbon components can have a desirable dielectric constant (κ-value), for example a dielectric constant of less than about 7, including less than about 6, and less than about 5.5. For example, a silicon nitride film including boron and carbon components may have a dielectric constant between about 4.8 and about 6, including between about 4.8 and about 5.5.

In some embodiments, a silicon nitride ALD deposition process can be used to deposit a silicon nitride (SiN) film of a desired thickness and composition. ALD type processes are based on controlled, self-limiting surface reactions. Gas phase reactions are avoided by contacting the substrate alternately and sequentially with reactants. Vapor phase reactants are separated from each other in the reaction chamber, for example, by removing excess reactants and/or reactant byproducts from the reaction chamber between reactant pulses. For example, the ALD deposition process can include contacting a substrate with a silicon reactant such that the silicon reactant adsorbs on the substrate surface, and subsequently contacting the substrate with a nitrogen reactant. A silicon reactant may comprise silicon-containing compounds which can contribute silicon to the growth of the silicon nitride film. A nitrogen reactant may comprise nitrogen-containing compounds which can contribute nitrogen to the growth of the silicon nitride film. Exposure of the substrate to the silicon reactant and the nitrogen reactant can be repeated as many times as required to achieve a film of a desired thickness and composition. Excess reactants may be removed from the vicinity of the substrate, for example by purging from the reaction space with an inert gas, after each contacting step. For example, the reactor chamber may be purged between reactant pulses. The flow rate and time of each reactant, is tunable, as is the purge step, allowing for control of the dopant concentration and depth profile in the film. In some embodiments, the substrate can be moved to a space free or substantially free of reactants prior to purging the reactor chamber of the excess reactants and/or reaction byproducts.

In some embodiments, an ALD process for depositing the silicon nitride (SiN) film can include one or more cycles, each cycle comprising at least two distinct processes or phases. The provision and removal of a reactant from the reaction space may be considered a phase. In a first process or phase, a first reactant comprising silicon is provided and forms no more than about one monolayer on the substrate surface. This reactant is also referred to herein as “the silicon precursor” or “silicon reactant.” In a second process or phase, a second reactant comprising a nitrogen-containing compound is provided and reacts with the adsorbed silicon precursor to form SiN. This second reactant may also be referred to as a “nitrogen precursor” or “nitrogen reactant.” As described herein, the second reactant may comprise ammonia (NH₃) and/or another suitable nitrogen-containing compound. Additional processes or phases may be added and phases may be removed as desired to adjust the composition of the final film. In some embodiments for depositing a silicon nitride (SiN) film, one or more deposition cycles typically begins with provision of the silicon precursor followed by the nitrogen precursor. In some embodiments, one or more deposition cycles begins with provision of the nitrogen precursor followed by the silicon precursor. One or more of the reactants may be provided with the aid of a carrier gas, such as nitrogen (N₂), argon (Ar) and/or helium (He).

In some embodiments, a process for depositing a silicon nitride film comprising boron and carbon components (SiN(B, C)) having desirable characteristics can include a hybrid process comprising both an ALD process and a CVD process. For example the process for forming a silicon nitride film comprising boron and carbon components can comprise an ALD portion for depositing silicon nitride and a CVD portion for incorporating boron and carbon components into the growing film. The silicon nitride and boron and carbon components may in some embodiments form a continuous film in which the silicon nitride and boron and carbon components do not form distinct layers or substantially do not form distinct layers.

In some embodiments, no plasma is used in the deposition of the silicon nitride film comprising boron and carbon components. For example, a process for depositing the silicon nitride film comprising boron and carbon components can include both a thermal ALD process and a thermal CVD process, including a pulsed thermal CVD process. In some embodiments, plasma of a nitrogen precursor is used in the ALD process for depositing the silicon nitride. For example, a PEALD process comprising plasma for a nitrogen precursor may be used for depositing silicon nitride, and the PEALD process may be combined with a thermal CVD process for incorporating boron and carbon components into the silicon nitride.

In some embodiments, the process for depositing a silicon nitride film comprising boron and carbon components (SiN(B, C)) can include an ALD process for depositing a silicon nitride (SiN) film (e.g., an ALD process comprising alternately and sequentially contacting the substrate with a silicon reactant, for example comprising octachlorotrisilane (Si₃Cl₈, OCTS), and a nitrogen reactant, for example comprising ammonia (NH₃)), and a decomposition process in which one or more boron reactants decomposes on the substrate surface for introducing the boron and carbon components into the silicon nitride film (e.g., a CVD process using one or more boron reactants, for example comprising triethylboron (B(C₂H₅)₃, TEB, in which the TEB decomposes). In some embodiments, the ALD process for depositing the SiN film can include contacting the substrate with a silicon reactant comprising hexachlorodisilane (Si₂Cl₆, HCDS). In some embodiments, the CVD process for introducing boron and carbon components can include contacting the substrate with a boron reactant comprising trialkylboron, such as trimethylboron (B(CH₃)₃, TMB or triethylboron (TEB)). In some embodiments, excess reactants and/or reaction by products can be removed by a purge step after each process (e.g., a purge step can be performed after a silicon reactant pulse, a nitrogen reactant pulse and/or a boron reactant pulse). For example, excess silicon reactants and/or reaction byproducts can be removed from the reaction space prior to introducing the nitrogen reactants, such that the nitrogen reactant reacts with the adsorbed silicon reactant to form a monolayer of silicon nitride on the substrate. In some embodiments, the substrate can be moved to a space free or substantially free of reactants prior to purging the reaction space.

In some embodiments a pulsed CVD process is used for the decomposition process. In some embodiments a pulsed CVD process is used in which multiple short pulses of the boron reactant are provided. In some embodiments a single, longer pulse of the boron reactant is provided. In some embodiments the conditions are selected such that under the same conditions the SiN is formed from surface reactions (ALD) while the boron reactant decomposes (CVD). In some embodiments, a pulsed CVD process for introducing boron and carbon components into the SiN film facilitates integration of the boron carbon process. In some embodiments, a pulsed CVD process for introducing boron and carbon components into the SiN film facilitates increased control in the quantity of boron and carbon components incorporated into the SiN film. In some embodiments, the boron reactant can also be provided under ALD conditions.

According to some embodiments of the present disclosure, the pressure of the reaction chamber during processing is maintained at about 0.01 Torr to about 50 Torr, preferably from about 0.1 Torr to about 10 Torr.

One or more parameters of the process for depositing the silicon nitride film and/or the process for introducing the boron and carbon components can be adjusted to provide a film having desired characteristics. For example, a flow rate of one or more boron reactants, and/or a process temperature, of a CVD process for introducing the boron carbon and components can be adjusted. For example, a duration of a reactant pulse for providing one or more boron reactants in a pulsed CVD process can be adjusted. In some embodiments, one or more parameters of the ALD process for depositing the SiN film can be adjusted, such as a process temperature, a reactor chamber pressure, and/or a reactant exposure duration.

In some embodiments, the process for depositing a silicon nitride film comprising boron and carbon components can include one or more cycles of the process for providing the silicon nitride SiN film (e.g., repetitions of the SiN process), and/or one or more cycles of the process for introducing the boron and carbon components (e.g., repetitions of the boron carbon process). In some embodiments, the number of repetitions of the SiN process and the boron carbon process can be tuned to provide a film of desirable characteristics. In some embodiments, the ratio of the number of repetitions of the SiN process to the number of repetitions of the boron carbon process is selected to give a desired film composition. In some embodiments, the SiN process cycle is repeated 2, 3, 4, 5, 6, 7, 8, 9, 10, or more times, for each boron carbon process cycle. In some embodiments, a number of repetitions of the SiN process cycle is followed by a number of repetitions of the boron carbon process cycle, where the number of repetitions of the SiN process cycle is different from the number of repetitions of the boron carbon process cycle.

In some embodiments, a process for depositing a silicon nitride film comprising boron and carbon components can include a sequence comprising a number of repetitions of an ALD process for deposition of the silicon nitride SiN film and/or a number of repetitions of a CVD process for introducing the boron and carbon components, the number of repetitions of each of the ALD process, the CVD process, and/or the total number of repetitions in the sequence of both the ALD process and CVD process being selected to provide a film having desired characteristics and/or a desired boron and carbon components composition. For example, a boron and carbon content may be adjusted to provide a film having a desired etch performance (e.g., a wet etch rate and/or a dry etch rate), and/or conformality performance. In some embodiments, the number of repetitions of the CVD process can be selected based on one or more parameters of the CVD process and/or the ALD process. In some embodiments, the number of repetitions of the ALD process can be selected based on one or more parameters of the ALD process and/or the CVD process. In some embodiments, the sequence including the number of repetitions of the ALD process cycle and the number of repetitions of the CVD process cycle can be repeated to provide a film of a desired composition and/or thickness.

In some embodiments, the process for depositing a silicon nitride film comprising boron and carbon components does not include a plasma enhanced process. That is, no plasma is used during the entire process. For example, the process can include both a thermal ALD process and a pulsed thermal CVD process (e.g., thermal decomposition of one or more boron reactants, such as decomposition of TEB).

FIG. 13 is a flow chart of an example of a process flow 700 for forming a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film). In block 702, a substrate can be exposed to one or more vapor phase silicon reactants (e.g., one or more silicon precursors). A layer of silicon reactant is formed on the substrate surface. In some embodiments, the one or more vapor phase silicon reactants can adsorb onto a surface of the substrate. In some embodiments the one or more silicon reactants at least partially decomposes at the substrate surface. In block 704, the substrate can be exposed to one or more vapor phase nitrogen reactants (e.g., a nitrogen precursor). For example, the one or more nitrogen reactants may interact with the one or more silicon reactants on the surface of the substrate (e.g., the one or more nitrogen reactants may react with the one or more silicon reactants on the substrate surface to form silicon nitride (SiN)). In block 706, the substrate can be exposed to one or more vapor phase boron reactants (e.g., one or more boron and/or carbon precursors). The one or more boron reactants may react with the silicon nitride on the substrate surface, thus introducing boron and carbon components into the film such that a silicon nitride film comprising boron and carbon components is formed. In some embodiments the one or more boron reactants decomposes on the substrate surface.

In some embodiments, one or more of the reactants may at least partially decompose on the substrate surface. For example, one or more of the silicon, nitrogen or boron reactants is provided under chemical vapor deposition (CVD) conditions.

In some embodiments, a process for exposing a substrate to a silicon reactant, a nitrogen reactant, and/or a boron reactant can include a chemical vapor deposition (CVD) process. In some embodiments, each of exposing a substrate to a silicon reactant, a nitrogen reactant, and a boron reactant can include a CVD process, including for example a pulsed CVD process.

In some embodiments, exposing a substrate to a silicon reactant, a nitrogen reactant, and/or a boron reactant can include a vapor phase deposition process in which one or more reactants decompose to facilitate formation of the SiN(B, C) film.

In some embodiments, the ALD and/or the CVD processes can be a plasma enhanced process (e.g., a direct plasma process and/or a remote plasma process). In some embodiments, the ALD and/or the CVD processes do not include a plasma enhanced process. For example, the ALD process can be a thermal ALD process.

In some embodiments, a process for exposing a substrate to a silicon reactant, a nitrogen reactant, and/or a boron reactant may overlap, or be combined. For example, one or more of the silicon reactant, nitrogen reactant, and/or boron reactant may be provided in pulses that partially or completely overlap.

In some embodiments, a nitrogen-containing gas (e.g., nitrogen gas (N₂) and/or ammonia (NH₃)) can be fed continuously throughout a process for depositing a SiN(B, C) film (e.g., the nitrogen-containing gas can serve as a carrier gas and/or as a reactant). For example, the nitrogen-containing gas can serve as a carrier gas for reactants in a plasma process (e.g., used for generating a nitrogen-containing plasma). In some embodiments, the nitrogen-containing gas is fed continuously or substantially continuously into the reaction chamber throughout a deposition process, for example including while reactant pulses of a silicon reactant and/or a boron reactant are introduced into the reactor chamber. Nitrogen-containing gas flow rate and/or a concentration of the nitrogen flow can be adjusted during the deposition process, for example, during pulsing of the silicon reactant and/or boron and/or carbon reactant.

A variety of silicon reactants may be suitable. In some embodiments, a suitable silicon reactant in a process for depositing a silicon nitride film can include at least one of silicon halides, silicon alkylamines, silicon amines and/or silanes (e.g., including silanes comprising one or more alkyl groups). For example, a suitable silicon reactant can include a silicon chloride. In some embodiments, a silicon reactant can include a halosilane. In some embodiments, a silicon reactant can include an alkyl silicon compound comprising a halide. In some embodiments, a silicon reactant can be alkyl silane. In some embodiments, a silicon reactant can include octachlorotrisilane (Si₃Cl₈, OCTS). In some embodiments, a silicon reactant can include hexachlorodisilane (Si₂Cl₆, HCDS).

Suitable nitrogen reactants can include a variety of nitrogen-containing reactants. In some embodiments, a nitrogen reactant can include a hydrogen bonded to a nitrogen (N—H). In some embodiments, a suitable nitrogen reactant can be ammonia (NH₃). In some embodiments, a suitable nitrogen reactant can be hydrazine (N₂H₄). In some embodiments, a suitable nitrogen reactant can comprise one or more reactive species generated by a nitrogen-containing plasma, including for example nitrogen-containing radicals. In some embodiments, a suitable nitrogen reactant can include nitrogen atoms.

In some embodiments, a suitable boron reactant can include a boron compound having at least one organic ligand. In some embodiments, the organic ligand can have double and/or triple bonds. In some embodiments, the organic ligand can be a cyclic ligand. In some embodiments, the organic ligand can comprise delocalized electrons. In some embodiments, a suitable boron reactant can include trialkylboron compounds. In some embodiments, a suitable boron reactant can include triethylboron (B(C₂H₅)₃, TEB). In some embodiments, a suitable boron reactant can include trimethylboron (B(CH₃)₃, TMB). In some embodiments, a suitable boron reactant can include trialkylboron compounds having linear or branched alkyl groups, including for example linear or branched C₃-C₈, and more preferably including linear or branched C₃-C₅. Suitable boron reactants can include a variety of other boron-containing reactants. In some embodiments, a boron reactant can include a boron halide, an alkylboron, and/or a borane. In some embodiments, a boron reactant can include boron halides, borane halides and complexes thereof. For example, a suitable boron halide can have a boron to halide ratio of about 0.5 to about 1.

Suitable boranes can include compounds according to formula I or formula II.

B_(n)H_(n+x)   (formula I)

Wherein n is an integer from 1 to 10, preferably from 2 to 6, and x is an even integer, preferably 4, 6 or 8.

B_(n)H_(m)   (formula II)

Wherein n is an integer from 1 to 10, preferably form 2 to 6, and m is an integer different than n, from 1 to 10, preferably from 2 to 6.

Of the above boranes according to formula I, examples include nido-boranes (B_(n)H_(n+4)), arachno-boranes (B_(n)H_(n+6)) and hyph-boranes (B_(n)H_(n+8)). Of the boranes according to formula II, examples include conjuncto-boranes (B_(n)H_(m)). Also, borane complexes such as (CH₃CH₂)₃N—BH₃ can be used.

In some embodiments, suitable boron reactants can include borane halides, particularly fluorides, bromides and chlorides. An example of a suitable compound is B₂H₅Br. Further examples comprise boron halides with a high boron/halide ratio, such as B₂F₄, B₂Cl₄ and B₂Br₄. It is also possible to use borane halide complexes.

In some embodiments, halogenoboranes according to formula III can be suitable boron reactants.

B_(n)X_(x)   (formula III)

Wherein X is Cl or Br and n is 4 or an integer from 8 to 12 when X is Cl, or n is an integer from 7 to 10 when X is Br.

In some embodiments, carboranes according to formula IV can be suitable boron reactants.

C₂B_(n)H_(n+x)   (formula IV)

Examples of carboranes according to formula IV include closo-carboranes (C₂B_(n)H_(n+2)), nido-carboranes (C₂B_(n)H_(n+4)) and arachno-carboranes (C₂B_(n)H_(n+6)).

In some embodiments, amine-borane adducts according to formula V can be suitable boron reactants.

R₃NBX₃   (formula V)

Wherein R is linear or branched C1 to C10, preferably C1 to C4 alkyl or H, and X is linear or branched C1 to C10, preferably C1 to C4 alkyl, H or halogen.

In some embodiments, aminoboranes where one or more of the substituents on B is an amino group according to formula VI can be suitable boron reactants.

R₂N   (formula VI)

Wherein R is linear or branched C1 to C10, preferably C1 to C4 alkyl or substituted or unsubstituted aryl group.

An example of a suitable aminoborane is (CH₃)₂NB(CH₃)₂.

In some embodiments, a suitable boron reactant can include a cyclic borazine (—BH—NH—)₃ and/or its volatile derivatives.

In some embodiments, alkyl borons or alkyl boranes can be suitable boron reactants, wherein the alkyl is typically linear or branched C1 to C10 alkyl, preferably C2 to C4 alkyl.

In some embodiments, the substrate on which deposition of a silicon nitride film comprising boron and carbon is desired, such as a semiconductor workpiece, is loaded into a reactor chamber. The reactor chamber may be part of a cluster tool in which a variety of different processes in the formation of an integrated circuit are carried out. In some embodiments, one or more deposition processes described herein can be performed in a batch reactor, including for example in a mini-batch reactor (e.g., a reactor having a capacity of eight substrates or less) and/or a furnace batch reactor (e.g., a reactor having a capacitor of fifty or more substrates). In some embodiments, one or more deposition processes described herein can be performed in a single wafer reactor. In some embodiments, a spatial reactor chamber may be suitable (e.g., a spatial ALD reactor chamber). In some embodiments, a reactor chamber having a cross-flow configuration can be suitable. In some embodiments, a reactor chamber having a showerhead configuration can be suitable.

Exemplary single wafer reactors are commercially available from ASM America, Inc. (Phoenix, Ariz.) under the tradenames Pulsar® 2000 and Pulsar® 3000 and ASM Japan K.K (Tokyo, Japan) under the tradename Eagle® XP and XP8. Exemplary batch ALD reactors are commercially available from and ASM Europe B.V (Almere, Netherlands) under the tradenames A400™ and A412™.

FIG. 14 is a flow chart showing another example of a process 800 for forming a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film). The process 800 can include a sequence 802 having a process 804 for forming silicon nitride on a substrate surface and a process 812 for introducing boron and carbon components into the silicon nitride. In some embodiments, the sequence 802 can be repeated a number of times to form a SiN(B, C) film having a desired composition and/or thickness. The ratio of the number of times process 804 is performed to the number of times the process 812 is performed can be varied to tune the concentration of boron and carbon components in the film and thus to achieve a film with desired characteristics. For example, the number of times process 804 is repeated relative to the number of times the process 812 is repeated can be selected to provide a film with desired boron and carbon components content.

The process 804 for forming silicon nitride on a substrate surface can include blocks 806, 808 and 810. In block 806, the substrate can be exposed to one or more silicon reactants. In block 808, the substrate can be exposed to one or more nitrogen reactants. In block 810, blocks 806 and 808 can be repeated a number of times (e.g., a number of cycles of the process 804). In some embodiments, exposing the substrate to the one or more silicon reactants in block 806 can comprise exposing the substrate to a silicon reactant pulse, and exposing the substrate to the one or more nitrogen reactants in block 808 can comprise exposing the substrate to a nitrogen reactant pulse. In some embodiments, a silicon reactant pulse of block 806 and a nitrogen reactant pulse of block 808 are separated by a purge step (not shown) configured for removing excess silicon reactant and/or reaction byproduct from the reactor chamber. A purge step may comprise flowing of purge gas, and/or evacuating the reactor chamber (e.g., by drawing a vacuum upon the reactor chamber) so as to remove or substantially remove excess reactants and/or reaction byproducts. In some embodiments, excess nitrogen reactant and/or reaction byproducts are removed prior to performing the repetition process in block 810, for example by performing a purge step (not shown) after exposing the substrate to the one or more nitrogen reactants in block 808. In some embodiments, process 804 is an ALD process. In some embodiments, process 804 is a CVD process, where at least one of the reactants at least partially decomposes on the substrate surface. In some embodiments, the pulses of the silicon and nitrogen reactants may at least partially overlap.

The process 812 for introducing boron and carbon components into the silicon nitride can include blocks 814 and 816. In block 814, the substrate can be exposed to one or more boron reactants. In block 816, block 814 can be repeated a number of times (e.g., a number of cycles of the process 812). In some embodiments, exposing the substrate to the one or more boron reactants comprises exposing the substrate to a boron reactant pulse. For example, in block 816, the boron reactant pulse of block 814 can be repeated a number of times. In some embodiments, each boron reactant pulse can be separated by a purge step (not shown) configured to remove excess boron reactants and/or reaction byproducts. In some embodiments, a single boron reactant pulse is provided (e.g., a repetition of process 814 is not performed). The one or more boron reactants are provided under CVD conditions in some embodiments, such that the one or more boron reactants decompose on the substrate surface.

In some embodiments, a process for forming a SiN(B, C) film (e.g., process 800 of FIG. 14) can be a hybrid process including both ALD and CVD processes. For example, a process for forming the silicon nitride (SiN) film (e.g., process 804 of FIG. 14) can include an ALD process, and a process for introducing boron and carbon components into the silicon nitride (SiN) film (e.g., process 812 of FIG. 14, so as to form a SiN(B, C) film) can include a CVD process.

In some embodiments plasma is not used in either of 804 or 812. For example, process 804 and/or 812 can include a thermal process, such as a thermal ALD process and/or a thermal CVD process.

A silicon reactant of an ALD process for providing a silicon nitride film (SiN) may comprise octachlorotrisilane (Si₃Cl₈, OCTS) and/or hexachlorodisilane (Si₂Cl₆, HCDS), and a nitrogen reactant of the ALD process may comprise ammonia (NH₃). Exposing a substrate to the silicon reactant (e.g., block 806 of FIG. 14) can include exposing the substrate to Si₃Cl₈ and/or Si₂Cl₆. For example, Si₃Cl₈ and/or Si₂Cl₆ can be fed into a reactor chamber (e.g., a silicon reactant pulse) for a duration of time, including for example with the aid of a nitrogen carrier gas. Exposing the substrate to the nitrogen reactant (e.g., block 808 of FIG. 14) can include exposing the substrate to NH₃. For example, NH₃ can be fed into a reactor chamber (e.g., a nitrogen reactant pulse) for a duration of time, including for example with the aid of a nitrogen carrier gas. The pulse length for a silicon reactant pulse and/or a nitrogen reactant pulse can be from about 0.05 seconds to about 5.0 seconds, about 0.1 seconds to about 3 seconds or about 0.2 seconds to about 1.0 second. For example, a nitrogen reactant pulse and/or a silicon reactant pulse can be about 1 second.

As described herein, a reactant pulse for delivering one or more reactants into a reactor chamber in an ALD process can be followed by a purge step, such as for removal of an excess reactant and/or a reaction byproduct from the vicinity of the substrate surface. A gas such as nitrogen (N₂), argon (Ar) and/or helium (He) can be used as a purge gas to aid in the removal of the excess reactant and/or reaction byproduct. In some embodiments, a purge step of an ALD process can be about 1 second to about 20 seconds, about 1 second to about 15 seconds or about 1 second to about 10 seconds, including about 5 seconds. For example, one cycle of an ALD process for exposing a substrate to a silicon reactant and/or a nitrogen reactant can include a reactant pulse of about 0.5 seconds, followed by a purge step of about 5 seconds. In some embodiments, one cycle of an ALD process can include a silicon reactant pulse of about 0.5 seconds, followed by a purge step of about 5 seconds, followed by a nitrogen reactant pulse of about 0.5 seconds, and then followed by a purge step of about 5 seconds.

A cycle of the ALD process may be repeated a number of times until a film of the desired thickness and/or composition is obtained. In some embodiments the deposition parameters, such as the reactant flow rate, reactant flow duration, purge step duration, and/or reactants themselves, may be varied in one or more deposition cycles during the ALD process in order to obtain a film with the desired characteristics. For example, one or more deposition parameters of an ALD process cycle may be different from that of another ALD process cycle.

As described herein, in some embodiments, a process for depositing a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) can include a chemical vapor deposition (CVD) process. A CVD process for introducing boron and carbon components into a silicon nitride film can include decomposition of one or more reactants and/or chemical interaction between multiple reactants on the silicon nitride film. For example, a reactant can be fed into a reactor chamber, the decomposition of which facilitates formation of the desired film. In some embodiments, a suitable boron reactant can include triethylboron (B(C₂H₅)₃, TEB) and/or trimethylboron (B(CH₃)₃, TMB). For example, TEB fed into the reactor chamber may decompose on the silicon nitride film to facilitate introduction of boron and carbon components into the silicon nitride film.

In some embodiments, a pulsed CVD process can be used. In some embodiments, the process for depositing the SiN(B, C) film includes an ALD process configured to provide a silicon nitride SiN film on a substrate surface, and a CVD process performed subsequent to at least one cycle of the ALD process, the CVD process being configured for introducing boron and carbon components into the silicon nitride film so as to form the SiN(B, C) film (e.g., a pulsed CVD process for delivering pulses of one or more boron reactants into the reactor chamber). In some embodiments, the CVD process can be repeated a number of times to provide a SiN(B, C) film having a desired composition (e.g., repeating for a number of times a cycle of a CVD process including a reactant pulse followed by a purge process). In some embodiments, the CVD process for introducing boron and carbon components is not a pulsed CVD process, such that a boron reactant is fed in a continuous or substantially continuous stream into the reactor chamber to achieve a SiN(B, C) film having a desired boron and carbon components content.

A pulsed CVD process can include feeding a reactant gas (e.g., a reactant pulse) into a reactor chamber for a duration of time. In some embodiments, the reactant pulse of a CVD process can have a duration from about 0.05 seconds to about 5.0 seconds, about 0.1 seconds to about 3 seconds or about 0.2 seconds to about 1.0 second. For example, a reactant pulse can be about 0.5 seconds.

In some embodiments, an interval between two reactant pulses can comprise discontinuing flow of the one or more reactants of the reactant pulse. An interval between reactant pulses may have a duration of about 1 second to about 20 seconds, including about 1 second to about 15 seconds, or about 1 second to about 10 seconds. For example, the interval can be about 5 seconds. In some embodiments, the interval comprises transport of the substrate to a space free or substantially free of reactants. In some embodiments, the interval comprises a purge step. For example, the interval may comprise transport of the substrate to a space free or substantially free of reactants, and a purge step. For example, a pulse for delivering one or more reactants into a reactor chamber for a pulsed CVD process can be followed by a purge step, such as for removal of an excess reactant and/or a reaction byproduct from the vicinity of the substrate surface. A purge step can include flow of one or more inert gases through the reactor chamber (e.g., argon (Ar), helium (He), and/or nitrogen (N₂)). In some embodiments, each reactant pulse can be followed by a purge step. A purge step can include removal of an excess reactant and/or byproducts from the vicinity of the substrate. In some embodiments, a purge step of a CVD process can have a duration of about 1 second to about 20 seconds, about 1 second to about 15 seconds or about 1 second to about 10 seconds. For example, a purge process can be about 5 seconds. Other durations for the reactant pulse and/or the purge process may also be suitable, as can be determined by the skilled artisan given the particular circumstances.

A suitable duration of time in which a reactant gas is provided into a reactor chamber and/or a duration of a purge step, a gas flow rate in the reactant pulse and/or the purge step, can depend on one or more parameters of the reaction process, for example, adjusting a reactant pulse duration and/or reactant pulse gas flow rate, and/or a purge step duration and/or purge step gas flow rate, such that desired reactants are provided to and/or removed from the vicinity of the substrate surface.

As described herein, a process for depositing a SiN(B, C) film can include a sequence (e.g., sequence 802 of FIG. 14) having a number of repetitions of a process for providing a silicon nitride film, followed by a number of repetitions of a process for introducing boron and carbon components into the silicon nitride film. In some embodiments, the sequence can be repeated for a number of times (e.g., the sequence being repeated Z number of times) to provide a SiN(B, C) film having a desired composition and/or thickness. For example, a process for forming a SiN(B, C) film can include a sequence having a number cycles of an ALD processes for depositing a silicon nitride SiN film followed by a number of cycles of an CVD process for introducing boron and carbon components into the silicon nitride SiN film, the sequence being repeated for a number of times to provide a SiN(B, C) film of a desired composition and/or thickness.

In some embodiments, a sequence, including a number of cycles of an ALD process for depositing a silicon nitride film followed by a number of cycles of a CVD process for introducing boron and carbon components into the silicon nitride film, can be repeated about 1 time to about 150 times, including about 25 times to about 75 times. For example, the sequence can be repeated about 75 times. For example, the sequence can be repeated 100 times.

A number of cycles of a process for providing a silicon nitride (SiN) film (e.g., X cycles of an ALD process, such as repeating a number of times or performing a number of cycles of process 804 of FIG. 14) and/or a number of cycles of a process for introducing boron and carbon components into the silicon nitride (e.g., Y cycles of a CVD process, such as repeating a number of times or performing a number of cycles of process 812 of FIG. 14) in a sequence may be selected to achieve desired film characteristics. For example, a sequence can include a number of cycles of an ALD process followed by a number of cycles of a CVD process. The number of ALD cycles and/or the number of CVD cycles may be varied to provide a SiN(B, C) film comprising a desired composition and/or thickness. For example, the number of cycles of the process for introducing boron and carbon components can be selected to provide a SiN(B, C) film having a desired boron and carbon components content (e.g., for demonstrating a desired etch rate, conformality performance, and/or other film characteristic).

In some embodiments, the number of cycles of a process for providing boron and carbon components of the silicon nitride film within a sequence can be from about one cycle to about twenty cycles, including from about one cycle to about ten cycles. In some embodiments, the process for providing the boron and carbon components can be repeated five times. For example, a pulsed CVD process for introducing boron and carbon components into a silicon nitride film can be repeated three times within a sequence. The cycling of the process for providing the boron and carbon components can be performed prior to additional cycling of a process for depositing a silicon nitride SiN film. For example, a sequence of a SiN(B, C) film deposition process can include first cycling a number of times a process for depositing a silicon nitride SiN film, and second followed by cycling for a number of times a process for adding the boron and carbon components to the SiN film.

In some embodiments, a ratio of a number of cycles of a process for depositing a silicon nitride film to a number of cycles of a process for introducing a boron and carbon components (e.g., a ratio of Y:X) within a sequence can be about 1:1 to about 100:1, including about 3:1 to about 50:1. In some embodiments, the ratio of the number of cycles for the process of depositing a silicon nitride film to the number of cycles of the process for introducing boron and carbon components within a sequence can be about 5:1 to about 20:1. The ratio can be expressed as a percentage or a boron carbon process fraction, such as a percentage of the total number of cycles in a sequence which is a process for introducing the boron and carbon components. For example, a boron carbon process fraction or a percentage of the total number of cycles in a sequence which is a process for introducing the boron and carbon components can be adjusted to provide a SiN(B, C) film having desired composition. The percentage or boron carbon process fraction may be calculated by the following formula: X/(X+Y)*100%. In some embodiments, the boron carbon process fraction or the percentage of the total number of cycles in a sequence which is a process for introducing the boron and carbon components can be about 0.01% to about 50%, including about 5% to about 20%. For example, the boron carbon process fraction can be about 10%. For example, a process having a boron carbon process fraction of about 5.0% to about 10% can form a SiN_(x)(B_(y), C_(z)) film where x can be about 1.3 to about 1.8, y can be about 0.5 to about 1.5, and z can be about 0.3 to about 1.3.

A first phase and/or a second phase of an ALD process, and/or a CVD process can be performed at a process temperature of about 25° C. to about 800° C., including about 100° C. to about 600° C. The process temperature as referred to herein can comprise a temperature of a reactor chamber susceptor, a reactor chamber wall, and/or a temperature of the substrate itself. In some embodiments, a first phase and/or a second phase of an ALD process and/or a CVD process can be performed at a process temperature of about 150° C. to about 500° C. For example, one or both of the first phase and the second phase of the ALD process, and/or the CVD process can be performed at a process temperature of about 200° C. to about 400° C. For example, a first phase and/or a second phase of one or more cycles of an ALD process described herein may be performed in a reactor chamber having a susceptor, a substrate and/or a reactor chamber wall heated to a temperature of about 200° C. to about 400° C., such as a temperature of about 400° C. For example, the CVD process can be performed in a reactor chamber having a susceptor, a substrate and/or a reactor chamber wall heated to a temperature of about 400° C. In some embodiments, the CVD process for introducing boron and carbon components into the silicon nitride can be performed at a process temperature of less than 400° C., including for example from about 325° C. to about 400° C., and about 350° C. to about 400° C.

In some embodiments, a temperature of a process for depositing a silicon nitride SiN film and/or a process for introducing a boron and carbon components can be sufficiently high to facilitate a decomposition of one or more reactants (e.g., a silicon reactant and/or a nitrogen reactant of an ALD process, and/or a boron reactant of a CVD process), and/or reaction between reactants and/or between reactants and the substrate surface, while providing a process with a reduced thermal budget. In some embodiments, a process temperature for depositing the silicon nitride SiN film and/or introducing boron and carbon components can be about 325° C. to about 800° C., including about 350° C. to about 600° C., about 400° C. to about 600° C., or about 375° C. to about 450° C. For example, a CVD process for introducing boron and carbon components into a silicon nitride can be performed at a process temperature of about 400° C. (e.g., a CVD process including decomposing the boron reactant TEB for introducing the boron and carbon components to the silicon nitride film). In some embodiments, an ALD process for depositing the silicon nitride SiN film can be performed at a process temperature of about 400° C. (e.g., an ALD process in which one or more reactants may decompose in forming the SiN film). In some embodiments, a temperature of the ALD process can be different from a temperature of the CVD process. In some embodiments, the same temperature is used for the ALD process for forming the silicon nitride SiN film and the CVD process for adding boron and carbon components to the SiN film.

An example of a deposition process for forming a SiN(B, C) film can be performed (e.g., in a Pulsar® 3000 chamber, commercially available from ASM America, Inc. of Phoenix, Ariz.) using a thermal ALD process for forming a silicon nitride SiN film. The thermal ALD process can be performed at a process temperature of about 400° C. on a 300 millimeter (mm) wafer, including a silicon reactant comprising octachlorotrisilane (Si₃Cl₈, OCTS) fed into the reactor chamber with a carrier gas (e.g., nitrogen) such that a silicon reactant pulse has a duration of about 1 second and is followed by a purge process (e.g., using purge gas comprising nitrogen) having a duration of about 5 seconds. The OCTS may be stored in a bubbler at a temperature of about 40° C. and provided into the reactor chamber from the bubbler (e.g., a mass flow rate of the OCTS may be controlled by controlling the extent to which a valve for delivering the OCTS into the reactor chamber is kept open). The thermal ALD process can include a nitrogen reactant comprising ammonia (NH₃) fed into the reactor chamber such that the nitrogen reactant pulse has duration of about 1 second and which is followed by a purge process (e.g., using purge gas comprising nitrogen) having a duration of about 5 seconds. The NH₃ may be provided into the reactor chamber from a gas source maintained at a pressure of about 1.5 Bar (e.g., a mass flow rate of the NH₃ may be controlled by controlling the extent to which a valve for delivering the NH₃ into the reactor chamber is kept open). The ALD process can be cycled a number of times. A number of cycles of the ALD process can be followed by a number of cycles of a thermal CVD process for introducing boron and carbon components into the SiN film. The thermal CVD process can be performed at a temperature of about 400° C. and can include a boron reactant pulse for providing a boron reactant comprising triethylboron (B(C₂H₅)₃, TEB) into the reactor chamber, where the boron reactant pulse can have a duration of about 0.5 seconds. The boron reactant pulse may be followed by a purge step (e.g., using purge gas comprising nitrogen) having a duration of about 5 seconds. For example, the SiN(B, C) deposition process can include a sequence comprising 19 cycles of the ALD process followed by 2 cycles of the CVD process (e.g., providing a boron carbon process fraction of about 10%), where the sequence is repeated 75 times.

A composition of a silicon nitride film comprising boron and carbon components may be adjusted, for example, by increasing or decreasing a boron carbon process fraction of the process for depositing the film. For example, a boron and carbon content of the film may be adjusted by adjusting a boron carbon process fraction of the film fabrication process. In some embodiments, the silicon nitride film comprising boron and carbon components can have about 0.1 atomic % to about 50 atomic % of boron, including about 1 atomic % to about 35 atomic % of boron. For example, the silicon nitride film comprising boron and carbon components can have about 5 atomic % to about 30 atomic % boron. In some embodiments, the silicon nitride film comprising boron and carbon components can have about 0.1 atomic % to about 50 atomic % of carbon, including about 1 atomic % to about 35 atomic % of carbon. For example, the silicon nitride film comprising boron and carbon components can have about 5 atomic % to about 30 atomic % carbon. In some embodiments, a silicon and/or a nitrogen content can be adjusted by adjusting a boron carbon process fraction of the film fabrication process.

In some embodiments, a SiN(B, C) film formed according to one or more processes described herein can have a desirable dielectric constant (κ-value). A dielectric constant of a SiN(B, C) film may be lower than that of conventional silicon nitride films. In some embodiments a SiN(B, C) film can have a dielectric constant less than about 7, including less than about 6. For example, a SiN(B, C) film may have a dielectric constant between about 4.8 and about 7, including between about 4.8 and 6, and between about 4.8 and about 5.5. In some embodiments, a dielectric constant of a SiN(B, C) film can be adjusted by adjusting a boron carbon process of the film fabrication process. In some embodiments, a SiN(B, C) film having a dielectric constant of about 5.5 can be formed using a deposition process having a boron carbon process fraction of about 10% or higher. SiN(B, C) films with reduced dielectric constants, for example dielectric constants less than that of conventional silicon nitride films, used for certain applications of a semiconductor device (e.g., as a spacer material for a transistor gate feature) may facilitate improvements in one or more device electrical parameters, including a reduction in device parasitic capacitances.

As described herein, a SiN(B, C) film can be a sacrificial film in a semiconductor device fabrication process. For example, the SiN(B, C) film may be selectively removed in an etch process. In some embodiments, a sacrificial SiN(B, C) film can be selectively removed during fabrication of a semiconductor device using an etch process comprising chlorine (Cl) and/or fluorine (F), such as chlorine and/or fluorine containing plasma processes. In some embodiments, a SiN(B, C) film may form a part of a finished semiconductor device. For example, the SiN(B, C) film may be more resistant to etch than one or more other materials used in the fabrication of the semiconductor device.

The SiN(B, C) film may have a desired etch selectivity with respect to another material in the device. For example, an etch selectivity of the SiN(B, C) film may be tuned by adjusting a boron and carbon components content of the film (e.g., by adjusting a boron carbon process fraction of the film fabrication process). In some embodiments, the SiN(B, C) film may be etched by a dry etch process and/or a wet etch process. For example, the SiN(B, C) film may be etched by a plasma etch process, including a fluorine-containing plasma. In some embodiments, the SiN(B, C) film can have a etch selectivity (e.g., a dry etch and/or a wet etch selectivity) of about 5 or greater with respect to another material of the device, including a selectivity of about 10 or greater, about 20 or greater, or about 50 or greater.

In some embodiments, the SiN(B, C) film can demonstrate a desired wet etch selectivity, such as a wet etch selectivity with respect to a thermal silicon oxide (TOX) layer. For example, the SiN(B, C) film may be more resistant to wet etch than the thermal silicon oxide layer, having a ratio of a wet etch rate of the SiN(B, C) film to a wet etch rate of a thermal silicon oxide layer less than about 1, less than about 0.5, or less than about 0.3. In some embodiments, the ratio of a wet etch rate of the SiN(B, C) film to a wet etch rate of the thermal silicon oxide layer can be less than about 0.1.

In some embodiments, one or more silicon nitride films comprising boron and carbon components (SiN(B, C)) formed according to one or more processes described herein can have a desired etch rate in a number of etchant solutions. In some embodiments, a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) may be resistant or substantially resistant to one or more wet etchants. For example, a SiN(B, C)) film can have an etch rate of less than about 1 nanometers per minute (nm/min), including less than about 0.5 nm/min, including less than about 0.2 nm/min and including less than about 0.1 nm/min, in one or more of the following etchant solutions at the provided temperatures: a concentrated nitric acid HNO₃ solution (e.g., a solution having a HNO₃ concentration of about 65 to about 75 weight %) at about 80° C., a 5.5 weight % hydrofluoric acid (HF) at room temperature (e.g. a temperature of about 25° C.), a solution having a ratio of nitric acid:hydrofluoric acid:water (HNO₃:HF:H₂O) at about 1:1:5 at about room temperature (e.g., a temperature of about 25° C.), an aqueous solution of sodium hydroxide (NaOH) having a concentration of NaOH of about 10 weight % at about room temperature (e.g., a temperature of about 25° C.), a concentrated hydrochloric acid (HCl) solution (e.g., a solution having an HCl concentration of about 35 to about 40 weight %) at about room temperature (e.g., a temperature of about 25° C.), and a concentrated sulfuric acid solution (H₂SO₄) (e.g., a solution having a H₂SO₄ concentration of greater than about 90 weight %) at about room temperature (e.g., a temperature of about 25° C.).

In some embodiments, a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) may be resistant or substantially resistant to a wet etchant comprising phosphoric acid (H₃PO₄) at a concentration of about 85 weight % at about room temperature (e.g., a temperature of about 25° C.). In some embodiments, a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) may be resistant or substantially resistant to one or more of the following wet etchants (e.g., an etch rate of less than about 3 nanometers/min (nm/min)), and after a dip in a 1 weight % hydrofluoric acid (HF) for about 2 minutes): phosphoric acid (H₃PO₄) at a concentration of about 85 weight % at about room temperature (e.g., a temperature of about 25° C.), aqueous sodium hydroxide (NaOH) having a concentration of about 10 weight % solution at about room temperature (e.g., a temperature of about 25° C.), a hydrochloric acid (HCl) solution having a concentration of about 35 to about 40 weight % (e.g., about 37 weight %) at about room temperature (e.g., a temperature of about 25° C.), and a sulfuric acid solution (H₂SO₄) having a concentration of greater than about 90 weight % (e.g., 98 weight %) at about room temperature (e.g., a temperature of about 25° C.).

In some embodiments, a SiN(B, C) film can have an etch rate of more than about 1.0 nanometers per minute (nm/min) in a solution having a ratio of hydrogen peroxide:hydrofluoric acid:water (H₂O₂:HF:H₂O) of about 5:5:90, by volume, at about room temperature (e.g., at a temperature of about 25° C.). In some embodiments, a SiN(B, C)) film can be etched subsequent to being exposed to a treatment in oxygen-containing atmosphere, including for example ozone and/or an oxygen-containing plasma (e.g., a plasma comprising oxygen atoms and/or other oxygen-containing radicals).

As described herein, a SiN(B, C) film may be deposited on and/or over a three-dimensional (3-D) structure while demonstrating desired conformality or step coverage. In some embodiments, a SiN(B, C) film can demonstrate desired conformality or step coverage over a three-dimensional structure having an aspect ratio of about 2:1 or higher, including about 3:1 or higher, about 5:1 or higher, or about 8:1 or higher. In some embodiments, a SiN(B, C) film can demonstrate desired conformality or step coverage over a three-dimensional structure having an aspect ratio of about 10:1 or higher, about 25:1 or higher, or about 50:1 or higher. In some embodiments, a SiN(B, C) film can demonstrate a desired step coverage over one or more features as described herein, including a step coverage of about 80% or higher, including about 90% or higher, about 95% or higher, or about 100%. In some embodiments, a SiN(B, C) film can demonstrate a step coverage of about 80% or higher, including about 90% or higher, about 95% or higher, or about 100%, when formed on three-dimensional structures having an aspect ratio of up to about 250:1, including up to about 150:1 and up to about 100:1.

In some embodiments, a portion of a SiN(B, C) film deposited on a sidewall of a three-dimensional structure can demonstrate a desired etch rate, for example, as compared to an etch rate of a portion of the film deposited on a top surface of the three-dimensional feature. In some embodiments, a portion of a SiN(B, C) film deposited on a sidewall of a three-dimensional structure can demonstrate a uniform or substantially uniform etch rate of the SiN(B, C) film as a portion of the SiN(B, C) film deposited on a top surface of the structure. For example, a ratio of an etch rate of a sidewall portion of the SiN(B, C) film to an etch rate of a top surface portion of the SiN(B, C) film can be less than about 4, including less than about 2, about 1.5. In some embodiments, the ratio is about 1.

In some embodiments, a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) can be subjected to an annealing process subsequent to its formation. In some embodiments, the SiN(B, C) film can be annealed in an inert gas atmosphere (e.g., an atmosphere comprising nitrogen and/or one or more noble gases). For example, the annealing process may be performed in a nitrogen atmosphere at a temperature of about 600° C. or higher, about 800° C. or higher, or 1000° C. or higher. In some embodiments, the SiN(B, C) film can be annealed at a temperature of up to about 900° C. In some embodiments, the SiN(B, C) film can be annealed in a hydrogen atmosphere, such as at a temperature of about 600° C. or higher, about 800° C. or higher, or 1000° C. or higher, including up to about 900° C. In some embodiments, a boron and carbon component of the SiN(B, C) film does not diffuse out of the film when annealed in a nitrogen atmosphere at a temperature of up to about 900° C. In some embodiments annealing can be carried out in a hydrogen or inert gas atmosphere, for example at a temperature of about 600° C. or higher, about 800° C. or higher, or 1000° C. or higher.

Examples of SiN(B, C) Films

FIG. 15A graphs the compositions (e.g., as measured by rutherford backscattering spectrometry (RBS)) of four films having a boron carbon process fraction (e.g., a percentage of the total number of cycles of which are cycles of the process for introducing a boron and carbon content into a silicon nitride SiN film) from about 0% to about 15%. The atomic percent of silicon, nitrogen, boron, carbon and chlorine of each of the four films are shown, with the atomic percent of silicon, nitrogen, boron and carbon shown with reference to the left vertical axis and the atomic percent of chlorine shown with reference to the right vertical axis. Each of the four films can be formed according to one or more processes as described herein. For example, SiN films and SiN(B, C) films of varying composition can be deposited using a deposition process performed in a Pulsar® 3000 chamber (e.g., commercially available from ASM America, Inc. of Phoenix, Ariz.) using a thermal ALD process for forming a silicon nitride SiN film. The thermal ALD process can be performed at a temperature of about 400° C., and a pressure of about 0.1 Torr to about 10 Torr, on a 300 millimeter (mm) wafer, including a silicon reactant comprising octachlorotrisilane (Si₃Cl₈, OCTS) fed into the reactor chamber with a carrier gas (e.g., nitrogen) such that a silicon reactant pulse has a duration of about 1 second and is followed by a purge step (e.g., using purge gas comprising nitrogen) having a duration of about 5 seconds. The OCTS may be stored in a bubbler at a temperature of about 40° C. and provided into the reactor chamber from the bubbler (e.g., a mass flow rate of the OCTS may be controlled by controlling the extent to which a valve for delivering the OCTS into the reactor chamber is kept open). The thermal ALD process can include a nitrogen reactant comprising ammonia (NH₃) fed into the reactor chamber such that the nitrogen reactant pulse has duration of about 1 second and which is followed by a purge step (e.g., using purge gas comprising nitrogen) having a duration of about 5 seconds. The NH₃ may be provided into the reactor chamber from a gas source maintained at a pressure of about 1.5 Bar (e.g., a mass flow rate of the NH₃ may be controlled by controlling the extent to which a valve for delivering the NH₃ into the reactor chamber is kept open). The ALD process can be cycled a number of times. A number of cycles of the ALD process can be followed by a number of cycles of a pulsed thermal CVD process for introducing boron and carbon components into the SiN film. The thermal CVD process can be performed at a temperature of about 400° C., and a pressure of about 0.1 Torr to about 10 Torr, and can include a boron reactant comprising triethylboron (B(C₂H₅)₃, TEB) fed into the reactor chamber where the boron reactant pulse can have a duration of about 0.5 seconds, the reactant pulse followed by a purge step (e.g., using purge gas comprising nitrogen) having a duration of about 5 seconds. For example, the SiN(B, C) deposition process can include a sequence including a number of cycles of the ALD process followed by one to three cycles of the CVD process (e.g., to provide boron carbon process fractions of about 0% to about 15%), where the sequence can be repeated a number of times (e.g., about 50 times to about 100 times). For example, the sequence may be repeated 75 times.

The graphs of FIG. 15A show that a boron and a carbon content of a film can increase with an increase in the boron carbon process fraction. For example, the boron and carbon components content can increase linearly or substantially linearly with an increase in the boron carbon process fraction. FIG. 15A shows that silicon content and nitrogen content can decrease with an increase in the boron carbon process fraction. For example, the silicon and/or nitrogen content can decrease linearly or substantially linearly with an increase in the boron carbon process fraction. FIG. 15A further shows that chlorine content can decrease with an increase in a boron carbon process fraction.

FIG. 15B graphs a film growth rate in angstroms per cycle (Å/cycle) of four films formed by fabrication processes having a boron carbon process fraction from about 0% to about 15%. A cycle, as shown in FIG. 15B, can correspond to a sequence including a number of cycles of a process for providing a silicon nitride SiN film and a number of cycles of a process for introducing boron and carbon into the SiN film (e.g., sequence 802 of FIG. 14). Each of the four films can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 15A. FIG. 15B shows that a film growth rate can decrease with an increase in a boron carbon process fraction. Without being limited by any particular theory or mode of operation, boron reactants adsorbed onto a surface of a substrate may reduce the ability of silicon reactants and/or nitrogen reactants to properly adsorb onto the surface of the substrate (e.g., silicon reactants and/or nitrogen reactants from a subsequent silicon nitride deposition process). Increasing a boron carbon process fraction (e.g., as increased amount of boron reactants are provided in a SiN(B, C) film fabrication process), may increasingly reduce the ability of silicon and/or nitrogen reactants from subsequent silicon nitride deposition processes to adsorb onto the substrate surface. Further, without being limited by any particular theory or mode of operation, the reduced ability of silicon and/or nitrogen reactants from subsequent silicon nitride deposition processes to adsorb onto the substrate surface may also result in a film having higher boron and carbon components content than would otherwise be expected based on the boron carbon process fraction.

In some embodiments, a film thickness non-uniformity (e.g., a one sigma (1σ) thickness non-uniformity) may not be negatively impacted by an increased boron carbon process fraction. In some embodiments, a film thickness non-uniformity remain the same or substantially the same with increased boron carbon process fraction. For example, a film thickness non-uniformity of a process for depositing a silicon nitride film having boron and carbon components can be less than about 20%, including less than about 10%, and about 5%. In some embodiments, a film thickness non-uniformity can be improved with a decrease in a boron carbon process fraction up to a particular value. For example, a boron carbon process fraction of less than about 10% can provide an improved film thickness non-uniformity.

Referring to FIG. 16, a Fourier Transform Infrared Spectroscopy (FTIR) analysis of four films having boron carbon process fractions from about 0% to about 15% is shown. Each of the four films can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 15A. The FTIR indicates presence of various features within each film, including for example the presence of various chemical bonds. For example, the FTIR analysis can show addition of features and/or changes in features of a film after being subject to a film fabrication process. Peaks corresponding to the various features of each film in FIG. 16 are labeled with an “O” or with an “*” to indicate an origin of the marked feature. For example, peaks in the graph marked by an “O” indicates that the features (e.g., a hydrogen bonded to a nitrogen (N—H), a hydrogen bonded to an oxygen (O—H), a hydrogen bonded to a silicon (Si—H), a nitrogen bonded to a silicon (Si—N)) are contributed by a process for depositing the silicon nitride SiN film. For example, peaks marked by an “*” indicate that the features (e.g., a hydrogen bonded to a carbon, a hydrogen bonded to a boron, a carbon bonded to a boron, a carbon bonded to another carbon, a boron bonded to another boron) are contributed by a process for introducing a boron and carbon components into the silicon nitride SiN film. FIG. 16 shows that a process for introducing the boron and carbon into the silicon nitride film can provide features such as a hydrogen bonded to a carbon (C—H) and/or a hydrogen bonded to a boron (B—H) (e.g., as shown in FIG. 16 between about 2500 cm⁻¹ and about 3000 cm⁻¹), and features such as a carbon bonded to a boron (B—C), a boron bonded to another boron (B—B) and/or a carbon bonded to another carbon (C—C) (e.g., as shown in FIG. 16 between about 1000 cm⁻¹ and about 1500 cm⁻¹, such as at about 1200 cm⁻¹). FIG. 16 shows a decrease in Si—H bonding features with an increase in the boron carbon process fraction. A reduction in Si—H bonding features may facilitate improved SiN(B, C) film performance, for example an improvement in an electrical property of the film. FIG. 16 also shows that a peak corresponding a nitrogen bonded to a silicon (Si—N) can shift to a higher wavenumber with an increase in the boron carbon process fraction, for example indicating a change in bonds between a silicon and a nitrogen.

FIG. 17 shows analysis based on X-ray reflectivity (XRR) measurements of four films having boron carbon process fractions from about 0% to about 15%. Film thickness in nanometers, film density in grams per cubic centimeter (g/cm³), and film roughness in nanometers (nm) are shown. Each of the four films can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 15A. FIG. 17 shows a decrease in a film density, and a slight increase in a film roughness, with an increase in a boron carbon process fraction.

FIG. 18 graphs wet etch rates, shown in nanometers per minute (nm/min) in a dilute HF solution (e.g., 0.5 weight % HF solution) of corresponding films formed by processes having various boron carbon process fractions. The films can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 9A. As shown in FIG. 18, a wet etch rate of a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) can decrease significantly with an increased boron carbon process fraction. FIG. 18 shows that film deposition processes having a boron carbon process fraction higher than about 5% can produce SiN(B, C) films having a significantly reduced wet etch rate. For example, a SiN(B, C) film having a desired wet etch rate in dilute HF may be formed by a process having a boron carbon process fraction of higher than about 10% (e.g., a SiN(B, C) film suitable for a spacer application).

FIGS. 19A-19D show wet etch performance of a silicon nitride film comprising boron and carbon components (e.g., a SiN(B, C) film) deposited on trench structures 1300 of a substrate. The film can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 15A. FIGS. 19A and 19C show scanning electron microscopy (SEM) images of the trench structures 1300 having the film 1302 on one or more surfaces of the trench structures 1300 prior exposing the film 1302 to a wet etchant. For example, a wet etchant comprising a dilute hydrofluoric acid (HF) solution is used (e.g., a 0.5 weight % HF solution) for a period of time (e.g., for about 2 minutes). FIGS. 19B and 19D show the film 1302 subsequent to exposure to the wet etchant. FIGS. 19B and 19D show that the film 1302 is unaffected or substantially unaffected by the wet etchant. For example, a ratio of the wet etch rate of the film 1302 to an etch rate of an underlying thermal oxide layer (e.g., thermal silicon dioxide, TOX) can be less than about 3:10. FIGS. 19B and 19D also show the film 1302 post wet etch providing conformal coverage of the trench structures 1300, for example, the film 1302 not delaminating from the underlying trench structures and/or not demonstrating other defects.

FIGS. 20A-20D show scanning electron microscopy (SEM) images of a SiN(B, C) film on surfaces of high aspect ratio trenches 1400 subsequent to being exposed to a wet etchant (e.g., subsequent to a dip in a dilute hydrofluoric acid (HF or dHF) solution, such as a 0.5 weight % HF solution) for a period of about 4 minutes. The film can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 15A. FIG. 20A is a lower magnification image, at 13 k× magnification, of the structures 1400, showing an upper portion 1402 of the trenches, a mid-section 1404 of the trenches, and a lower section 1406 of the trenches. The upper portion 1402 is shown at higher magnification, at 250 k× magnification in FIG. 20B, the mid-section 1404 is shown at higher magnification, at 250 k× magnification, in FIG. 20C, and the lower-section 1406 is shown in higher magnification, at 250 k× magnification, in FIG. 20D. As shown in FIGS. 20A-20D, the SiN(B, C) film can demonstrate excellent conformality or step coverage of the high aspect ratio trenches 1400 subsequent to being exposed to the wet etchant. For example, FIGS. 20A-20D show a SiN(B, C) film having a thickness of about 20 nm formed on an upper portion 1402 of the trench structure 1400, a thickness of about 20 nm formed on a mid-section 1404 of the trench structure 1400, and a thickness of about 19 nm formed on a lower portion 1406 of the trench structure 1400 (e.g., a conformality of about 95% or greater). A ratio of the wet etch rate of the SiN(B, C) film as shown in FIGS. 20A-20D to an etch rate of an underlying thermal oxide (e.g., thermal silicon dioxide, TOX) can be less than about 1:2.

FIGS. 21A-21D show scanning electron microscopy (SEM) images of a silicon nitride film comprising boron and carbon (e.g., a SiN(B, C) film) on surfaces of high aspect ratio trenches 1500 before being exposed to a wet etchant. The film can be formed according to one or more processes as described herein, such as the processes as described with reference to FIG. 15A. FIG. 21A is a lower magnification image, at 11 k× magnification, of the trench structures 1500, with FIG. 21B showing an upper portion 1502 of the trenches 1500 at a higher magnification of 200 k×, FIG. 21C showing a mid-section 1504 of the trenches 1500 at a higher magnification of 200 k×, and FIG. 21D showing a lower section 1506 of the trenches 1500 at a higher magnification of 200 k×. FIGS. 21A-21D show that the SiN(B, C) film can demonstrate excellent step coverage or conformality. For example, FIGS. 21B-21D show a SiN(B, C) film having a thickness of about 23 nm formed on an upper portion 1502 of the trench structure 1500, a thickness of about 23 nm formed on a mid-section 1504 of the trench structure 1500, and a thickness of about 24 nm formed on a lower portion 1506 of the trench structure 1500 (e.g., a conformality of about 95% or greater).

An etch rate of the SiN(B, C) film in the wet etchant (e.g., the wet etchant having the ratio of H₂O₂:HF:H₂O of about 5:5:90 by volume) can be about 1.1 nanometers per min (nm/min)±about 0.3 nm/min. In some embodiments, the SiN(B, C) film can be soaked in ozone (O₃) prior to being exposed to the wet etchant, for example to increase an etch rate of the film. An etch rate of the SiN(B, C) film soaked in ozone prior to being exposed to the wet etch can have a film etch rate of about 2.2 nm/min±about 0.5 nm/min. In some embodiments, the etch rates can vary depending on the film composition.

A SiN(B, C) film deposited on blanket silicon wafer analyzed by rutherford backscattering spectrometry (RBS) prior to and after a dip in a 0.5 weight % HF solution for about 2 minutes show that the composition of the as deposited film was: silicon (Si) 20 atomic %, nitrogen (N) 35 atomic %, boron (B) 20 atomic %, carbon (C) 18 atomic %, oxygen (O) 6 atomic %, chlorine (Cl) 1 atomic %. The composition of the film subsequent to being dipped in the HF solution was: Si 19 atomic %, N 30 atomic %, B 25 atomic %, C 19 atomic %, O 7 atomic %, Cl 1 atomic %. The RBS analysis shows that the composition of the film may not be significantly impacted by the HF dip process.

Although this disclosure has been provided in the context of certain embodiments and examples, it will be understood by those skilled in the art that the disclosure extends beyond the specifically described embodiments to other alternative embodiments and/or uses of the embodiments and obvious modifications and equivalents thereof. In addition, while several variations of the embodiments of the disclosure have been shown and described in detail, other modifications, which are within the scope of this disclosure, will be readily apparent to those of skill in the art based upon this disclosure. It is also contemplated that various combinations or sub-combinations of the specific features and aspects of the embodiments may be made and still fall within the scope of the disclosure. It should be understood that various features and aspects of the disclosed embodiments can be combined with, or substituted for, one another in order to form varying modes of the embodiments of the disclosure. Thus, it is intended that the scope of the disclosure should not be limited by the particular embodiments described above.

The headings provided herein, if any, are for convenience only and do not necessarily affect the scope or meaning of the devices and methods disclosed herein. 

What is claimed is:
 1. A method of doping a semiconductor substrate, comprising: depositing a boron and carbon film over the semiconductor substrate in a reaction space by exposing the substrate to a vapor phase boron precursor at a process temperature of 300° C. to 450° C., wherein the boron precursor comprises boron, carbon and hydrogen; and annealing the boron and carbon film at a temperature of 800° C. to 1200° C.
 2. The method of claim 1, wherein the vapor phase boron precursor decomposes on the substrate.
 3. The method of claim 1, wherein the vapor phase boron precursor comprises triethylboron or trimethylboron.
 4. The method of claim 1, wherein the vapor phase boron precursor is supplied to the reaction space with a carrier gas comprising argon.
 5. The method of claim 1, further comprising depositing a silicon oxide film on the substrate prior to depositing the boron and carbon film.
 6. The method of claim 1, wherein the boron and carbon film is deposited directly on the semiconductor substrate.
 7. The method of claim 1, further comprising depositing a boron dopant film on the substrate prior to depositing the boron and carbon film, wherein the boron dopant film is different from the boron and carbon film, and wherein the boron dopant film and the boron and carbon film are deposited sequentially and without exposing the substrate to ambient air between depositing the boron and carbon film and depositing the boron dopant film.
 8. The method of claim 1, further comprising maintaining a pressure of 0.5 Torr to 10 Torr within the reaction space during exposing the substrate to the vapor phase boron precursor.
 9. The method of claim 1, wherein the boron and carbon film has a thickness of up to 5 nm.
 10. A method of doping a substrate, comprising: depositing a boron and carbon film over a substrate in a reaction space using a chemical vapor deposition process, wherein depositing the boron and carbon film comprises: exposing the substrate to a vapor phase boron precursor in an inert gas atmosphere at a process temperature greater than 300° C.; and purging the reaction space subsequent to exposing the three-dimensional structure on the substrate to the vapor phase boron precursor; and annealing the boron and carbon film in a nitrogen atmosphere, wherein no cap layer is formed over the boron and carbon film prior to annealing.
 11. The method of claim 10, wherein depositing comprises depositing the boron and carbon film on a three-dimensional structure on the substrate.
 12. The method of claim 11, wherein the three-dimensional structure has an aspect ratio of greater than 8:1 and wherein the boron and carbon film has a step coverage of greater than 80%.
 13. The method of claim 10, wherein the boron and carbon film has a thickness of up to 5 nm.
 14. The method of claim 10, further comprising depositing a silicon oxide film on the substrate prior to depositing the boron and carbon film.
 15. The method of claim 10, wherein the vapor phase boron precursor is supplied to the reaction space with a carrier gas comprising argon.
 16. The method of claim 10, further comprising annealing at a temperature of 800° C. to 1200° C.
 17. A method of depositing a boron and carbon containing film on a substrate in a reaction space, comprising: contacting the substrate with a vapor phase boron precursor at a process temperature of 250° C. to 400° C. to form the boron and carbon containing film on the substrate, wherein the vapor phase boron precursor decomposes on the substrate, and wherein the film has a thickness of less than 30 angstroms.
 18. The method of claim 17, wherein the boron and carbon containing film has a thickness of less than 15 angstroms.
 19. The method of claim 18, wherein the boron and carbon containing film has a thickness of less than 5 angstroms.
 20. The method of claim 17, wherein the boron and carbon film is substantially resistant to dilute hydrofluoric acid solution.
 21. The method of claim 17, further comprising depositing the boron and carbon containing film in a batch reactor.
 22. The method of claim 17, further comprising forming at least one of a silicon oxide, an aluminum nitride, an aluminum oxide and a silicon nitride over the boron and carbon containing film in the reaction space.
 23. The method of claim 17, further comprising depositing the boron and carbon containing film over at least one of a silicon oxide, an aluminum nitride, an aluminum oxide and a silicon nitride.
 24. The method of claim 23, further comprising forming the at least one of the silicon oxide, aluminum nitride, an aluminum oxide and silicon nitride in the reaction space.
 25. The method of claim 17, wherein depositing the boron and carbon containing film comprises a cyclic process comprising at least two deposition cycles in which the substrate is contacted with the vapor phase boron precursor.
 26. The method of claim 25, wherein the cyclic process comprises less than 100 deposition cycles.
 27. The method of claim 17, wherein the boron and carbon containing film has a 1-sigma non-uniformity of less than 5%. 